JP2022107220A - Ferritic stainless steel sheet - Google Patents

Abstract

To provide a ferritic stainless steel sheet that has excellent corrosion resistance and can express excellent magnetic properties in DC and AC magnetic fields.SOLUTION: A ferritic stainless steel sheet is adopted that has a predetermined composition, satisfies Si+Al≥0.5 or more, and has a texture on the plate surface satisfying the following (a)-(c): (a) the area ratio of {110}±15° orientation grains is more than 2.0% to less than 20% with the angle difference of 15° or less between the normal direction of the steel sheet surface and the {110} orientation on the plate surface; (b) the area ratio of {100}±15° orientation grains is more than 2.0% to less than 20% with the angle difference of 15° or less between the normal direction of the steel sheet surface on the plate surface and the {100} orientation; and (c) C/(A+B)≤15.0 holds where the area ratio of the {110}±15° orientation grains is defined as A, the area ratio of the {100}±15° orientation grains is defined as B, and the area ratio of the {111}±15° orientation grains is defined as C on the plate surface.SELECTED DRAWING: None

Description

The present invention relates to a ferritic stainless steel sheet.

Ferritic stainless steel sheets are used in a wide range of fields such as home appliances, electronic devices, and automobiles. In particular, in fields where the material becomes hot, such as heating equipment, kitchen equipment, automobile fields, etc., the applied stainless steel is required to have oxidation resistance and corrosion resistance.

In addition, a motor case for accommodating stepping motors and hysteresis motors, motor parts such as motor cores, sensors such as electronic throttle sensors and EPS sensors, injectors, relays and electromagnetic valves, and their cores, yokes, connectors and housings. In such cases, magnetic characteristics are important. Especially in motor cases and motor parts, the plus and minus of the internal electrodes are frequently switched, so the magnetic characteristics in the AC magnetic field are important.

Specifically, the magnetic characteristics are determined from the values of saturation magnetic flux density (Bs), magnetic permeability (μ), residual magnetic flux density (Br), and coercive force (Hc). The saturation magnetic flux density Bs is an index showing the absolute value of the magnetic force of the material, and is the saturation magnetization that converges in a sufficiently large magnetic field H (A / m). The larger the saturation magnetic flux density Bs, the stronger the magnetic capacity shields the strong magnetic field. The magnetic permeability μ is an index of sensitivity to a magnetic field, and is calculated by the gradient (μ = B / H) of the magnetization B (T) with respect to the magnetic field H (A / m). The higher the magnetic permeability μ, the more sensitive the material is to the magnetic field and the easier it is to magnetize. Further, the residual magnetic flux density Br is the magnetic flux density remaining in the material when the magnetic field H is set to 0 from the state of the saturated magnetic flux density Bs. Furthermore, the coercive force Hc is a magnetic field value when the magnetic flux density becomes 0 after further demagnetization from this state. The smaller the residual magnetic flux density Br and the coercive force Hc, the easier it is to eliminate the magnetization.

In addition, regarding the magnetic characteristics in the AC magnetic field, the maximum magnetic flux density (Bm) at each frequency and the iron loss (W) that affects the value are important. Increasing the content of Fe, Ni, and Co is effective for increasing the maximum magnetic flux density, and in stainless steel, the content of Fe can be relatively increased by decreasing the Cr content. However, if the Cr content is lowered, the corrosion resistance, which is the most important property of stainless steel, is lowered.
Further, it is the eddy current induced in the magnetic material that causes the iron loss to increase. It is effective to increase the electrical resistivity in order to reduce the loss due to the eddy current. For example, high Cr-containing ferrite-based stainless steel has a high Cr content, which increases electrical resistivity and reduces iron loss, so the magnetic flux density tends to increase in the high frequency range, but it still tends to increase in the frequency range of 1 kHz or higher. It is difficult to prevent a decrease in magnetic flux density. Addition of Al or Si is effective for further increasing the electrical resistivity, but addition of Al or Si to a high Cr-containing ferritic stainless steel deteriorates toughness and workability.

In Patent Document 1, as a ferritic stainless steel plate having excellent magnetic properties, C ≦ 0.01%, Si: 0.1 to 0.6%, Mn: 0.1 to 1.0% in weight%. , S ≦ 0.004%, Cr: 5 to 13%, Ti: 0.05 to 0.5%, O ≦ 0.004%, N ≦ 0.015%, and C + N ≦ 0.015% A ferritic stainless steel sheet is described in which the balance is composed of Fe and unavoidable impurities, the sum of the (111) surface strengths in the surface layer and the central layer is 10 or less, and the maximum relative permeability ≥ 4000. Compared to copper, copper alloys or ceramics, it is excellent in impact resistance and magnetic properties, but the content of Al and Si is low, and it is not possible to secure a sufficient magnetic flux density in the high frequency range.

In Patent Document 2, as a ferritic stainless steel sheet having excellent magnetic properties, C: 0.015% or less, N: 0.015% or less, Si: 1.5% or less, Mn: 1.0 in weight%. A slab containing% or less, Cr: 10 to 14%, and Ti: 0.05 to 0.30% is hot-rolled to form a hot-rolled sheet, and then the hot-rolled sheet is cooled by a rolling reduction of 20 to 60%. Described are ferritic stainless steel sheets produced by interrolling and then annealing at 800-930 ° C. Compared to copper, copper alloys or ceramics, it is excellent in impact resistance and magnetic properties, but the content of Al and Si is low, and it is not possible to secure a sufficient magnetic flux density in the high frequency range.

Patent Document 3 describes C: 0.015 wt% or less, Si: 0.30 wt% or less, Mn: 0.30 wt% or less, Cr: 10.0 to 20.0 wt%, Mo: 0.5 to 2.0 wt%. %, Ti: 0.05 to 0.30 wt%, Cu: 0.3 to 1.5 wt% and Al: 0.05 to 1.5 wt%, and the balance is highly corrosion resistant with a substantially Fe composition. Although electromagnetic stainless steel is disclosed, corrosion resistance is ensured by adding Mo and Cu.

Patent Document 4 describes C: 0.02% or less, Si: 0.01 to 0.50%, Mn: 0.01 to 0.50%, Cr: 7.00 to 20.00%, Mo: 0. .30 to 2.00%, Cu: 0.10 to 2.00%, Ti: 0.05 to 0.50%, Al: 0.05 to 3.00%, B: 0.0005 to 0.05 % And N: 0.05% or less, and the balance is disclosed as a highly cold-forged electromagnetic stainless steel having a substantially Fe composition, but corrosion resistance is ensured by adding a composite of Ti, B, Mo, and Cu. ..

Patent Document 5 describes, in terms of mass%, C: 0.020% or less, Si: 1.00% or less, Mn: 1.00% or less, P: 0.035% or less, S: 0.0030% or less, Cr: 10.0 to 18.0%, N: 0.020% or less, Nb: 0.5% or less, Ti: 0.5% or less, Al: 0.10% or less, and the balance is Fe and impurities. A ferrite-based stainless steel plate having excellent magnetic properties is disclosed, which comprises the above, and the texture on the plate surface satisfies the following (i) and (ii).
(I) The area ratio of the {110} ± 15 ° azimuth grains in which the angle difference between the normal direction of the steel plate surface and the {110} plane orientation on the plate surface is within 15 ° is more than 3.0% and less than 30%.
(Ii) 0.10 <A / B <0.80, where A is the area ratio of the {110} ± 15 ° orientation grain and B is the area ratio of the {111} ± 15 ° orientation grain on the plate surface.

In Patent Document 6, in mass%, C: 0.020% or less, Si: 1.00% or less, Mn: 1.00% or less, P: 0.035% or less, S: 0.0030% or less, Cr: 10.0 to 18.0%, N: 0.020% or less, Nb: 0.5% or less, Ti: 0.5% or less, Al: 0.10% or less, Sn: 0.001 to 0 A ferritic stainless steel containing 5.5% and B: 0.005% or less and having an excellent magnetic property, characterized in that the balance is composed of Fe and impurities, is disclosed.

Japanese Patent No. 3629102 Japanese Unexamined Patent Publication No. 11-61255 Japanese Unexamined Patent Publication No. 2-305944 Japanese Unexamined Patent Publication No. 4-318153 Japanese Unexamined Patent Publication No. 2020-6473 Japanese Unexamined Patent Publication No. 2020-63472

The ferritic stainless steel sheet described in Patent Document 5 secures magnetic properties by controlling the crystal orientation, but Ni is not added and the Al content is low, so that sufficient magnetic properties may not be ensured. ..
The ferritic stainless steel sheet described in Patent Document 6 has improved magnetic properties by suppressing grain boundary segregation of P, S, etc. by adding Sn, which is a grain boundary segregation element, but Ni is added. In addition, since the Al content is low, it may not be possible to secure a sufficient magnetic flux density as in the case of the ferritic stainless steel plate described in Patent Document 5.

The present invention has been made in view of the above circumstances, and an object of the present invention is to provide a ferritic stainless steel sheet having excellent corrosion resistance and capable of exhibiting excellent magnetic properties in a DC magnetic field and an AC magnetic field.

In order to solve the above problems, the present invention has the following configurations.
[1] By mass%,
C: 0.001 to 0.030%,
Si: 0.01 to 3.00%,
Mn: 0.01-2.00%,
P: 0.030% or less,
S: 0.0050% or less,
Ni: 0.05 to 3.00%,
Cr: 5.0-18.0%,
Al: 0.001-5.000%,
V: 0.001 to 1.000%,
B: 0.0001 to 0.0100%, and N: 0.001 to 0.030%,
Further, it contains any one or two of Ti: 0.01 to 0.30% and Nb: 0.001 to 0.60%, the balance is Fe and impurities, and Si + Al ≧ 0.50 or more. Meet,
A ferritic stainless steel sheet characterized in that the texture on the plate surface satisfies the following (a) to (c).
(A) The angle difference between the normal direction of the steel plate surface and the {110} plane orientation on the plate surface is within 15 °, and the area ratio of the {110} ± 15 ° orientation grains is more than 2.0% and less than 20.0%. ..
(B) The angle difference between the normal direction of the steel plate surface and the {100} plane orientation on the plate surface is within 15 °. The area ratio of the {100} ± 15 ° orientation grains is more than 2.0% and less than 20.0%. ..
(C) On the plate surface, the area ratio of the {110} ± 15 ° orientation grains is A, the area ratio of the {100} ± 15 ° orientation grains is B, and the normal direction and {111} plane orientation of the steel plate surface on the plate surface. When the area ratio of the {111} ± 15 ° directional grain having an angle difference of 15 ° or less is C, C / (A + B) ≦ 15.0.
[2] Further, instead of a part of Fe, by mass%,
Mo: 0.01-3.00%,
Sn: 0.001 to 3.00%,
Cu: 0.01-3.00%,
W: 0.001 to 1.00%,
Sb: 0.001 to 0.100%,
Co: 0.001 to 0.500%,
Ca: 0.0001 to 0.0050%,
Mg: 0.0001 to 0.0050%,
Zr: 0.0001 to 0.0300%,
Ga: 0.0001 to 0.0100%,
Ta: 0.001 to 0.050%,
REM: 0.001 to 0.100%
The ferritic stainless steel sheet according to [1], which contains one or more of the above.

According to the present invention, it is possible to provide a ferritic stainless steel sheet having excellent corrosion resistance and capable of exhibiting excellent magnetic properties in a DC magnetic field and an AC magnetic field.
Further, the ferrite-based stainless steel plate of the present invention includes an injector housing, injector parts, a motor case for accommodating a stepping motor, a hysteresis motor, etc., motor parts such as a motor core, sensors such as an electronic throttle sensor and an EPS sensor, an injector and a relay. It can be suitably used for electromagnetic valves, their cores, yokes, connectors, housings, and the like.

The present inventors have made extensive studies for the purpose of providing a ferritic stainless steel sheet having excellent corrosion resistance and capable of exhibiting excellent magnetic properties in a DC magnetic field and an AC magnetic field. As a result, the following findings were found, and the present invention was made.

First, in stainless steel having a relatively low Cr content of 5 to 18% (hereinafter, also referred to as low Cr-containing steel or low Cr steel), the higher the Al and Si contents, the better the corrosion resistance. I found it. As a result, the low Cr-containing steel, which has excellent toughness and workability, contains a large amount of Al and Si, which also effectively improve the electrical resistivity, to ensure good toughness and workability, and the low Cr-containing steel. It is possible to improve the electrical resistivity and corrosion resistance, which are the problems of. That is, by adding a predetermined amount of Al and Si to the low Cr-containing steel, it is possible to provide a ferritic stainless steel having excellent magnetic characteristics in an AC magnetic field and good corrosion resistance as compared with the conventional case. Specifically, the ferrite-based stainless steel sheet according to the present invention can be obtained by setting Si + Al ≧ 0.50.

It was also found that by adding Ni in addition to Al and Si, improvement of corrosion resistance, improvement of toughness and improvement of magnetic properties can be achieved at the same time.
It has long been known that Ni improves the above three properties, but the effect of adding Ni is remarkable with respect to these three properties, especially in the low Cr high Al and Si-containing ferritic stainless steel according to the present invention. It was found that the effect was very beneficial. Regarding corrosion resistance, it is considered that since the present invention targets low Cr steel, the effect of suppressing active dissolution by adding Ni is greater than that of high Cr steel. Further, Al and Si are elements having an action of lowering toughness and magnetic properties (saturation magnetic flux density), and Ni also has an effect of improving these toughness and magnetic properties. That is, Ni is an important element that can improve the toughness and magnetic properties of the ferritic stainless steel according to the present invention.

Further, among the textures on the plate surface, the area ratios of the {110} ± 15 ° directional grains, the {100} ± 15 ° directional grains and the {111} ± 15 ° directional grains are controlled so as to be within a predetermined range. As a result, it was found that the magnetic properties of ferritic stainless steel can be improved.

As a specific method for controlling the texture, first, the crystal grain size is coarsened by setting the annealing temperature to 950 ° C. or higher during hot rolling plate annealing, and the area ratio of the crystal grains having a {100} plane orientation is increased. .. Next, the steel after annealing the hot-rolled plate is subjected to cold rolling with a reduction ratio of 60% or more to accumulate a large amount of strain in the coarsened crystal grains. This makes it possible to promote recrystallization of crystal grains having a {110} plane orientation during cold rolled sheet annealing. That is, by appropriately controlling the conditions for hot-rolled sheet annealing to increase the proportion of {100} ± 15 ° directional grains, and then cold-rolling at a reduction rate of 60% or more, during cold-rolled annealing, It is possible to sufficiently generate recrystallized grains having a {110} ± 15 ° plane orientation effective for magnetic properties.
Further, by setting the soaking temperature to 950 ° C. or lower at the time of annealing the cold-rolled sheet, it is possible to suppress the growth of crystal grains having a {111} plane orientation having an action of lowering the magnetic properties and toughness. Further, by setting the soaking temperature at the time of annealing the cold rolled plate to 950 ° C. or lower, fine precipitation of precipitates such as FeTiP can be promoted. This fine precipitate such as FeTiP has an effect of suppressing the growth of crystal grains having a {111} plane orientation during magnetic annealing. However, if the soaking temperature is high, the precipitates such as FeTiP become coarse, so that the effect of suppressing the growth of crystal grains having a {111} plane orientation during magnetic annealing cannot be enjoyed. That is, by appropriately controlling the soaking temperature at the time of cold-rolled plate annealing to 950 ° C. or lower, it is possible to promote the growth of crystal grains having a {100} plane or {110} plane orientation, and at the time of magnetic annealing. It is possible to suppress the growth of crystal grains having a {111} plane orientation, and as a result, it is possible to provide a ferritic stainless steel having excellent magnetic properties. The present inventors have found that the texture required to exhibit such characteristics after magnetic quenching is the structure having the above-mentioned plane orientation ratio.

Regarding the contribution of Al and Si to corrosion resistance, it is considered that Al promotes suppression of pitting corrosion growth and reimmobilization by leaching out as ions inside pitting corrosion at the initial stage of development and then adsorbing on the surface. Be done. Further, it is considered that Si forms an oxide inside the pitting corrosion and promotes suppression of pitting corrosion growth and reimmobilization. However, although neither Al nor Si has a sufficient effect of lowering the amount of active dissolution itself, it has been found that the amount of suppression of active dissolution can be ensured by adding Ni together with Al and Si.

Further, it is generally known that an Fe-based oxide having low corrosion resistance is formed on the surface during oxidation by magnetic annealing. However, when the ferrite-based stainless steel plate of the present invention is magnetically annealed, Al is formed. , It was found that it is difficult for this Fe-based oxide to be formed on the surface due to the high Si content. That is, in the present invention, Al and Si can also contribute to ensuring corrosion resistance after magnetic annealing.

Hereinafter, a ferritic stainless steel sheet according to an embodiment of the present invention will be described.
The ferrite-based stainless steel plate according to the present embodiment has C: 0.001 to 0.030%, Si: 0.01 to 3.00%, Mn: 0.01 to 2.00%, P: in mass%. 0.030% or less, S: 0.0050% or less, Ni: 0.05 to 3.00%, Cr: 5.0 to 18.0%, Al: 0.001 to 5.000%, V: 0 It contains .001 to 1.000%, B: 0.0001 to 0.0100%, N: 0.001 to 0.030%, and further Ti: 0.01 to 0.30% and Nb: 0. It contains any one or two of 001 to 0.60%, the balance is Fe and impurities, Si + Al ≥ 0.50 or more, and the texture on the plate surface is as follows (a) to (c). Meet.
(A) The area ratio of the {110} ± 15 ° azimuth grains in which the angle difference between the normal direction of the steel plate surface and the {110} plane orientation on the plate surface is within 15 ° is more than 2.0% and less than 20%.
(B) The area ratio of the {100} ± 15 ° azimuth grains in which the angle difference between the normal direction of the steel plate surface and the {100} plane orientation on the plate surface is within 15 ° is more than 2.0% and less than 20%.
(C) The area ratio of the {110} ± 15 ° orientation grains on the plate surface is A, the area ratio of the {100} ± 15 ° orientation grains is B, and the normal direction and {111} plane orientation of the steel plate surface on the plate surface. When the area ratio of the {111} ± 15 ° directional grain having an angle difference of 15 ° or less is C, C / (A + B) ≦ 15.0.
The chemical composition of the ferritic stainless steel sheet of the present embodiment will be described below. In addition, "%" display of the content of each element means mass%.

C: 0.001 to 0.030%
Since C lowers magnetic properties, intergranular corrosion resistance, and workability, it is necessary to keep its content low. Therefore, the C content is set to 0.030% or less. However, since excessively lowering the C content increases the refining cost, the C content is set to 0.001% or more. The preferable lower limit of the C content is 0.002% or more, the more preferable upper limit is 0.003% or more, and the further preferable upper limit is 0.004% or more. The preferable upper limit of the C content is 0.015% or less, and the more preferable upper limit is 0.010% or less.

Si: 0.01 to 3.00%
Si dramatically improves magnetic properties, electrical resistivity, oxidation resistance at medium and low temperatures (500 to 700 ° C.), and oxidation resistance at high temperatures (700 ° C. or higher). Moreover, it is a very useful element that not only concentrates on the surface to suppress the occurrence of corrosion but also reduces the corrosion rate of the base metal. Therefore, the Si content is set to 0.01% or more. However, since an excessive content of Si reduces toughness, workability, and weld penetration, the Si content is set to 3.00% or less. The preferable lower limit of the amount of Si is 0.05% or more, the more preferable range is 0.10% or more, and the more preferable range is 0.4% or more. The preferable upper limit of the Si content is 2.00% or less, the more preferable upper limit is 1.50% or less, and the further preferable upper limit is 1.20% or less.

Mn: 0.01-2.00%
Mn is useful as a deoxidizing element, but if an excessive amount of Mn is contained, the corrosion resistance is deteriorated. Therefore, the Mn content is set to 0.01 to 2.00%. The preferable lower limit of the Mn content is 0.05% or more, and the more preferable range is 0.10% or more. The preferred upper limit of the Mn content is 1.00% or less, and the more preferable upper limit is 0.50% or less.

P: 0.030% or less Since P is an element that deteriorates magnetic properties, workability, and weldability, the smaller the content, the better. Therefore, the P content is set to 0.030% or less. The preferred range of P content is 0.025% or less. However, since excessively lowering the P content increases the refining cost, the P content may be 0.001% or more.

S: 0.0050% or less Since S is an element that deteriorates corrosion resistance, the smaller the content, the better. Therefore, the S content is set to 0.0050% or less. The preferred range of S content is 0.0030% or less. However, since excessively lowering the S content increases the refining cost, the S content may be 0.0001% or more.

Ni: 0.05 to 3.00%
Ni is an important element in the present embodiment, and needs to be contained in an amount of 0.05% or more in order to improve magnetic properties, corrosion resistance, and toughness in a DC magnetic field. However, since the content of a large amount leads to an increase in alloy cost, the Ni content is set to 3.00% or less. The preferable lower limit of the Ni content is 0.06% or more, the more preferable lower limit is 0.10% or more, the further preferable lower limit is 0.13% or more, and the further preferable lower limit is 0.15% or more. The preferable upper limit of the Ni content is 2.50% or less, the more preferable upper limit is 2.00% or less, and the further preferable upper limit is 1.50% or less.

Cr: 5.0-18.0%
Cr must be contained in an amount of 5.0% or more in order to ensure oxidation resistance and corrosion resistance in a salt-damaged environment. As the Cr content is increased, the oxidation resistance and corrosion resistance are improved and the electrical resistivity is also increased, but the Cr content is 18 because the weld penetration, thermal conductivity, processability, toughness and manufacturability are lowered. It shall be 0.0% or less. The preferred range of Cr content is 7.5 to 15.0%, and the more preferable range is 9.0 to 13.0%.

Al: 0.001-5.000%
Al is an important element in this embodiment. Al dramatically improves the oxidation resistance of particularly high temperature (700 ° C. or higher). In addition, it is a very useful element that not only concentrates on the steel surface to suppress the occurrence of corrosion, but also reduces the corrosion rate of the base metal. Al also has the effect of increasing the electrical resistivity and improving the magnetic properties in an AC magnetic field. This effect is particularly remarkable in low Cr-containing stainless steel. Therefore, the Al content is set to 0.001% or more. However, since an excessive content of Al causes a decrease in toughness and elongation of the material and a decrease in toughness and processability, the Al content is set to 5.000% or less. The preferred range of Al content is 0.010 to 3.000%, and the more preferable range is 0.030 to 2.000%.

V: 0.001 to 1.000%
V needs to be contained in an amount of 0.001% or more in order to improve corrosion resistance. However, since the content of a large amount leads to an increase in alloy cost, the V content is set to 1.000% or less. The preferred range of V content is 0.005 to 0.800%, and the more preferable range is 0.010 to 0.500%.

B: 0.0001 to 0.0100%
B is an element useful for improving the secondary processability, and must be contained in an amount of 0.0100% or less. The lower limit of the B content is set to 0.0001% or more at which a stable effect can be obtained. The preferred range of B content is 0.0005 to 0.0050%, and the more preferable range is 0.0010 to 0.0030%.

N: 0.001 to 0.030%
N is an element useful for pitting corrosion resistance, but lowers magnetic properties, intergranular corrosion resistance, and workability. Therefore, it is necessary to keep the N content low. Therefore, the N content is set to 0.030% or less. However, since excessively lowering the N content increases the refining cost, the N content is set to 0.001% or more. The preferred range of N content is 0.002 to 0.020%.

Any one or two of Ti: 0.01 to 0.30% and Nb: 0.001 to 0.60% Ti and Nb are 0 in the case of Ti in order to prevent sensitization of stainless steel. It is necessary to contain 0.01% or more, and 0.001% or more in the case of Nb. However, since the content of a large amount leads to an increase in alloy cost, a decrease in toughness, a decrease in corrosion resistance due to an increase in inclusions in steel, and a decrease in manufacturability, the Ti amount is 0.30% or less and the Nb amount is 0.60% or less. The preferred range of Ti content is 0.03 to 0.25%, and the more preferable range is 0.04 to 0.20%. The preferred range of Nb content is 0.03 to 0.55%, and the more preferable range is 0.04 to 0.50%. Either one of Ti and Nb may be contained, and both Ti and Nb may be contained.

Further, regarding Al and Si, by satisfying Si + Al ≧ 0.50 (Al and Si are mass% of each element in the ferritic stainless steel), the magnetic characteristics in the AC magnetic field are excellent and the corrosion resistance is improved. be able to. Preferably, the total content of Si and Al (Si + Al) is 0.60 or more, more preferably 0.70 or more.

The above is the basic chemical composition of the ferritic stainless steel sheet of the present embodiment. That is, other than the above-mentioned elements, it is composed of Fe and impurities. However, in the present embodiment, the elements described below can be further contained as required.

Mo, Sn, Cu, W, Sb, Co, Ca, Mg, Zr, Ga, Ta, and REM may contain one or more of these depending on the purpose. The lower limit of these elements is 0% or more, preferably more than 0%.

Mo: 0.01 to 3.00%
Mo can be contained in an amount of 0.01% or more in order to improve corrosion resistance. However, the excessive content deteriorates the workability and is expensive, which leads to an increase in cost. Therefore, the Mo content is set to 3.00% or less. The preferred range of Mo content is 0.05 to 2.00%, and the more preferable range is 0.05 to 1.00%.

Sn: 0.001 to 3.00%
Sn can be contained in an amount of 0.001% or more in order to improve corrosion resistance. However, excessive content leads to increased costs. Therefore, the Sn content is set to 3.00% or less. The Sn content is preferably in the range of 0.005 to 1.00%, more preferably 0.010 to 1.00%.

Cu: 0.01 to 3.00%
Cu can be contained in an amount of 0.01% or more in order to improve corrosion resistance. However, excessive content leads to increased costs. Therefore, the Cu content is set to 3.00% or less. The preferred range of Cu content is 0.02 to 1.00%, and the more desirable range is 0.05 to 0.09%.

W: 0.001 to 1.00%
W can contain 1.00% or less in order to improve corrosion resistance. In order to obtain a stable effect, the W content is set to 0.001% or more. The preferred range of W content is 0.005 to 0.80%.

Sb: 0.001 to 0.100%
Sb can be contained in an amount of 0.100% or less in order to improve the total corrosion resistance. In order to obtain a stable effect, the Sb content is set to 0.001% or more. The preferred range of Sb content is 0.010 to 0.080%.

Co: 0.001 to 0.500%
Co can be contained in an amount of 0.500% or less in order to improve secondary processability and toughness. In order to obtain a stable effect, the Co content is 0.001% or more. The preferred range of Co content is 0.010 to 0.300%.

Ca: 0.0001 to 0.0050%
Ca is contained for desulfurization, but if it is contained in excess, water-soluble inclusions CaS are formed and the corrosion resistance is lowered. Therefore, Ca can be contained in the range of 0.0001 to 0.0050%. The preferred range of Ca content is 0.0005 to 0.0030%.

Mg: 0.0001 to 0.0050%
Mg has a finer structure and is also useful for improving workability and toughness. Therefore, Mg can be contained in the range of 0.0050% or less. In order to obtain a stable effect, the Mg content is 0.0001% or more. The preferred range of Mg content is 0.0005 to 0.0030%.

Zr: 0.0001 to 0.0300%
Zr can be contained in an amount of 0.0300% or less in order to improve corrosion resistance. In order to obtain a stable effect, the Zr content is set to 0.0001% or more. The preferred range of Zr content is 0.0010 to 0.0100%.

Ga: 0.0001 to 0.0100%
Ga can be contained in an amount of 0.0100% or less in order to improve corrosion resistance and hydrogen embrittlement resistance. In order to obtain a stable effect, the Ga content is 0.0001% or more. The preferred range of Ga content is 0.0005 to 0.0050%.

Ta: 0.001 to 0.050%
Ta can be contained in an amount of 0.050% or less in order to improve corrosion resistance. In order to obtain a stable effect, the Ta content is set to 0.001% or more. The preferred range of Ta content is 0.005 to 0.030%.

REM: 0.001 to 0.100%
Since REM has a deoxidizing effect and the like and is an element useful for refining, it can be contained in an amount of 0.100% or less. In order to obtain a stable effect, the REM amount is 0.001% or more. The preferred range of REM content is 0.003 to 0.050%.
Here, REM (rare earth element) refers to a general term for two elements, scandium (Sc) and yttrium (Y), and 15 elements (lanthanoids) from lanthanum (La) to lutetium (Lu), according to a general definition. .. REM is one or more kinds selected from these rare earth elements, and the content of REM is the total amount of rare earth elements.

The ferrite-based stainless steel sheet of the present embodiment is composed of Fe and impurities (impurities include unavoidable impurities) other than the elements described above. The "impurity" is one that is mixed in from ore, scrap, or the manufacturing environment as a raw material when steel is industrially manufactured, and is allowed as long as it does not adversely affect the steel sheet of the present invention. Means things. In addition to the elements described above, they can be contained within a range that does not impair the effects of the present invention. In the present embodiment, for example, Bi, Pb, Se, H and the like may be contained, but in that case, it is preferable to reduce as much as possible. On the other hand, the content ratio of these elements is controlled to the extent that the problem of the present invention is solved, and Bi is 0.01% or less, Pb is 0.01% or less, and Se is 0.01, if necessary. % Or less, H may contain 0.01% or less.

Next, the texture of the ferrite-based stainless steel sheet of the present embodiment will be described. In the ferrite-based stainless steel sheet of the present embodiment, the texture on the plate surface satisfies the following (a) to (c).

(A) The angle difference between the normal direction of the steel plate surface and the {110} plane orientation on the plate surface is within 15 °, and the area ratio of the {110} ± 15 ° orientation grains is more than 2.0% and less than 20.0%. ..
(B) The angle difference between the normal direction of the steel plate surface and the {100} plane orientation on the plate surface is within 15 °. The area ratio of the {100} ± 15 ° orientation grains is more than 2.0% and less than 20.0%. ..
(C) On the plate surface, the area ratio of {110} ± 15 ° azimuth grains was A, the area ratio of {100} ± 15 ° azimuth grains was B, and the area ratio of {111} ± 15 ° azimuth grains was C. When C / (A + B) ≤ 15.0.

The {110} direction is called the Goss direction, and has good magnetic properties because the rolling direction coincides with the easily magnetized axis of iron. In this embodiment, it has been found that it is effective to control the area ratio of {110} ± 15 ° oriented grains on the plate surface. By including the area ratio of the {110} ± 15 ° azimuth grain in the range of more than 2.0% and less than 20.0%, it is possible to contribute to an increase in the magnetic characteristics particularly in a DC magnetic field. From the viewpoint of magnetic characteristics, the area ratio of the {110} ± 15 ° oriented grain is preferably 5.0% or more, more preferably 7.0% or more. It is preferable that the area ratio of the {110} ± 15 ° directional grains is large, but in order to make it excessively large, it is necessary to set the heat-rolled plate heat treatment temperature to 1100 ° C. or higher, which will be described later, and the descalability of the hot-rolled annealed plate becomes high. It deteriorates significantly. Therefore, the area ratio of the {110} ± 15 ° orientation grain is 20.0% or less, preferably 18.0% or more.

Further, as for the {100} ± 15 ° azimuth grain, it is effective to secure an area ratio of a predetermined value or more from the viewpoint of magnetic characteristics in a DC magnetic field, as in the case of the {110} ± 15 ° azimuth grain. I found out. By including the area ratio of the {100} ± 15 ° directional grain in the range of more than 2.0% and less than 20.0%, it is possible to contribute to an increase in magnetic characteristics in a DC magnetic field. From the viewpoint of magnetic characteristics, the area ratio of the {100} ± 15 ° oriented grain is preferably 5.0% or more, more preferably 7.0% or more. It is preferable that the area ratio of the {100} ± 15 ° directional grains is large, but in order to make it excessively large, it is necessary to set the heat-rolled plate heat treatment temperature to 1100 ° C. or higher, which will be described later, and the descalability of the hot-rolled annealed plate becomes high. It deteriorates significantly. Therefore, the area ratio of the {100} ± 15 ° oriented grain is 20.0% or less, preferably 18.0% or more.

Further, on the plate surface, the area ratio of the {110} ± 15 ° orientation grains is A (%), the area ratio of the {100} ± 15 ° orientation grains is B (%), and the normal direction of the steel plate surface on the plate surface. {111} ± 15 ° Orientation where the angle difference from the plane orientation is within 15 ° When the area ratio of the grain is C (%), C / (A + B) from the viewpoint of magnetic characteristics in a DC magnetic field. It is effective to set ≦ 15.0.

The {111} ± 15 ° orientation grain is the main orientation of the recrystallized texture, but it is effective to reduce the ratio of the area ratio C in order to enhance the magnetic characteristics. That is, by reducing the ratio C / (A + B) with the total area ratio (A + B) of the {110} ± 15 ° directional grains and the {111} ± 15 ° directional grains that effectively improve the magnetic characteristics, the magnetism Among the characteristics, the magnetic characteristics in a DC magnetic field can be improved. Therefore, C / (A + B) is set to 15.0 or less, preferably 10.0.

The area ratio C of the {111} ± 15 ° directional grain is not particularly limited, but it is preferably 70% or less because if it becomes excessively large, the magnetic characteristics may be deteriorated.

In the present embodiment, the "plate surface" is a region from the surface of the steel plate to t / 8 when the thickness of the steel plate is t, and t / 8 from the surface of the steel plate in the direction of both sides of the steel plate. The area up to the thickness of.

The texture and its area ratio can be analyzed using electron backscatter diffraction (hereinafter, EBSD). The crystal orientation group that contributes to the magnetic characteristics is the crystal orientation divided into three regions at the center of the plate thickness: {100} ± 15 ° orientation grain, {110} ± 15 ° orientation grain, and {111} ± 15 ° orientation grain. The map can be displayed and quantified. For example, on a surface parallel to the steel plate surface, EBSD is measured in a measurement region of 800 μm in the plate width direction and 2000 μm in the rolling direction at a magnification of 100 times, and the normal direction of the surface parallel to the steel plate surface and the {100} plane direction. , {110} plane orientation, and crystal grains whose angular difference from each of the {111} plane orientation is within 15 ° (that is, {100} ± 15 ° orientation grain, {110} ± 15 ° orientation grain, {111} ± It is possible to display a crystal orientation map of (15 ° orientation grains ± 15 ° orientation grains) and display the area ratio of each.

The thickness of the ferritic stainless steel sheet according to the present embodiment is not particularly limited, but may be 0.1 to 5.0 mm. By setting the thickness of the ferritic stainless steel sheet to 0.1 mm or more, it can be applied to various uses such as structural materials. The thickness of the ferritic stainless steel sheet is preferably 0.4 mm or more. Further, by setting the plate thickness to 5.0 mm or less, the structure necessary for improving the magnetic characteristics can be built in. The thickness of the ferritic stainless steel sheet is preferably 4.0 mm or less.

Next, a method for manufacturing the ferritic stainless steel sheet of the present embodiment will be described.

The method for producing a ferrite-based stainless steel plate according to the present embodiment comprises the steps of steelmaking-hot rolling-hot-rolled plate annealing / pickling-cold rolling-cold-rolled plate annealing. It may be appropriately determined as long as the effect of the present invention is not impaired, but from the viewpoint of controlling the crystal plane orientation, it is necessary to appropriately control the conditions of hot-rolled sheet annealing, cold rolling reduction rate, and cold-rolled sheet annealing. be.
Hereinafter, each step and conditions of the manufacturing method will be described in detail.

In steelmaking, a method in which steel containing the essential components and components added as necessary is melted in a converter and subsequently subjected to secondary refining is preferable. The molten steel is cast (continuously cast) into a slab. The slab is heated to a predetermined temperature and hot-rolled to a predetermined plate thickness by continuous rolling. Considering the crystal orientation of the final product, it is desirable that the slab heating temperature is 1190 ° C. or higher and 1300 ° C. or lower, and the slab thickness is 3.0 mm or higher and 300.0 mm or lower.

The annealing step after hot rolling (hot-rolled sheet annealing step) is an important step for ensuring proper crystal orientation and obtaining a structure having excellent magnetic properties. Specifically, the soaking temperature in the hot rolled sheet annealing is set to 950 ° C to 1100 ° C. When the soaking temperature of the hot-rolled plate annealing is less than 950 ° C., the angle difference between the normal direction of the steel plate surface and the {100} plane orientation on the plate surface is within 15 °. Since the growth is insufficient, the soaking temperature is set to 950 ° C. or higher. Further, if the soaking temperature of the hot-rolled sheet annealing is 1100 ° C. or higher, the toughness may be lowered due to the coarsening of the crystal grains and the descaling property may be deteriorated due to the thickening of the oxidation scale. do. Preferably, the soaking temperature of the hot rolled sheet annealing is 980 ° C. to 1080 ° C. The soaking time (holding time) in the hot-rolled sheet annealing is not particularly limited, but is preferably 10 seconds to 120 seconds from the viewpoint of completion of recrystallization.

After annealing the hot-rolled plate, pickling and cold rolling are carried out in sequence. At this time, the rolling reduction ratio for cold rolling is 60% or more. If the reduction rate is less than 60%, recrystallization may be insufficient at the time of subsequent annealing of the cold rolled sheet. In particular, the reduction rate is such that the recrystallization of {110} ± 15 ° directional grains, in which the angle difference between the normal direction of the steel plate surface and the {110} plane orientation on the plate surface is within 15 °, may be insufficient. It is 60% or more, preferably 65% or more. On the other hand, if the reduction rate becomes too high, the productivity may deteriorate. Therefore, the reduction rate is preferably 95% or less.

Cold rolling after pickling may be carried out by either a normal Z-Mill mill or a tandem mill, but the normal direction and {111} plane orientation of the steel plate surface on the plate surface in the subsequent cold-rolled plate annealing step. Z-Mill mill rolling is preferable in order to suppress recrystallization of {111} ± 15 ° oriented grains with an angle difference of 15 ° or less. In cold rolling, roll roughness, roll diameter, rolling oil, number of rolling passes, rolling speed, rolling temperature and the like may be appropriately selected within a general range. Intermediate annealing may be added during cold rolling.

For the final annealing after cold rolling (cold-rolled sheet annealing), it is effective to set the soaking temperature to 950 ° C. or lower from the viewpoint of suppressing the growth of crystal grains having the {111} plane orientation. Further, by setting the soaking temperature at the time of annealing the cold rolled plate to 950 ° C. or lower, fine precipitation of precipitates such as FeTiP can be promoted. Since this fine precipitate such as FeTiP has an effect of suppressing the growth of crystal grains having a {111} plane orientation during magnetic annealing, it is desirable to deposit finely during cold rolling plate annealing. That is, the soaking temperature of cold-rolled sheet annealing is important from the viewpoint of suppressing the growth of crystal grains having a {111} plane orientation and promoting fine precipitation of precipitates such as FeTiP. In particular, the soaking temperature needs to be 850 ° C to 950 ° C. If the soaking temperature of the cold rolled sheet annealing is less than 850 ° C., recrystallization may be insufficient, so the soaking temperature is set to 850 ° C. or higher. Further, if the soaking temperature of the cold rolled sheet annealing exceeds 950 ° C., the growth suppression of the crystal grains having the {111} plane orientation may be insufficient, so the soaking temperature is set to 950 ° C. or lower. Preferably, the soaking temperature of the cold rolled sheet annealing is 880 ° C. to 920 ° C. The soaking time (holding time) in the cold rolled sheet annealing is not particularly limited, but is preferably 10 seconds to 120 seconds from the viewpoint of promoting recrystallization.

The intermediate annealing performed during cold rolling and the final annealing after cold rolling may be batch annealing or continuous annealing. Further, the atmosphere of each annealing may be bright annealing, which is annealed in a non-oxidizing atmosphere such as hydrogen gas or nitrogen gas, if necessary, or may be annealed in the atmosphere. After the final annealing, salt treatment, pickling, electrolytic pickling, etc. may be performed.

The ferritic stainless steel sheet according to the present embodiment can be produced by the production method described above, but steps other than the above may be appropriately performed as long as the effects of the present invention are not impaired. For example, final annealing. Later, a tension leveler step for shape correction may be carried out, or a plate may be passed through.

The ferritic stainless steel sheet according to this embodiment can be suitably used for applications requiring particularly magnetic characteristics. In that case, it is possible to obtain a product having excellent magnetic characteristics by subjecting it to magnetic annealing after processing the part. The conditions for magnetic quenching may be appropriately determined according to the applicable product, application, etc., but for example, in a vacuum of 1 × 10 ⁻² to 9 × 10 ⁻² Pa, the heating rate is 1 to 100 ° C./min. It is desirable that the soaking temperature is 800 to 1000 ° C. and the soaking time is 1 to 10 hours, and more preferably the soaking time is 1 to 3 hours. After such magnetic annealing, cooling with Ar gas or the like may be performed, or air cooling or furnace cooling may be performed. By performing such magnetic annealing, processing strain is removed and crystal grains are coarsened, magnetic characteristics are improved, and magnetic flux density can be improved. As a result, the magnetic characteristics in the DC magnetic field and the AC magnetic field can be improved.

The ferritic stainless steel sheet according to the present embodiment and its preferred manufacturing method have been described above. However, the ferritic stainless steel sheet of the present embodiment has excellent corrosion resistance and excellent magnetism in a DC magnetic field and an AC magnetic field. It is possible to provide a ferritic stainless steel sheet capable of exhibiting characteristics. Further, by applying the optimum magnetic annealing to the ferritic stainless steel sheet, it is possible to provide a ferritic stainless steel having excellent corrosion resistance and magnetic properties in a DC magnetic field and an AC magnetic field, which is suitable for applications requiring magnetic properties. ..

Hereinafter, the present invention will be described in more detail based on Examples, but the present invention is not limited to the conditions used in the following Examples. The underlined lines in the table indicate those outside the scope of the present invention.

The steels having the compositions shown in Tables 1A and 1B were melted, and slabs having a thickness of 200 mm were hot-rolled to a plate thickness of 3 mm. The slab heating temperature was in the range of 1190 to 1300 ° C. The notation "-" in the table means that it was not intentionally added.
Next, the hot-rolled steel sheet was subjected to heat treatment (hot-rolled sheet annealing) at the temperatures shown in Tables 2A and 2B for 60 seconds, and further subjected to sandblasting and pickling. Then, cold rolling was performed using a Zendimia mill at the rolling reduction rates shown in Tables 2A and 2B so as to have the plate thicknesses shown in Tables 2A and 2B. Then, heat treatment (cold-rolled sheet annealing) was performed for 60 seconds at the temperatures shown in Tables 2A and 2B, and then salt treatment and pickling were performed. For pickling, electrolytic pickling was performed in a solution having a nitric acid concentration of 150 g / L. In this way, a ferritic stainless steel sheet was manufactured.

A test piece having a width of 75 mm and a length of 150 mm was cut out from the vicinity of the center in the width direction of the produced steel sheet to prepare a test piece for the JASO-CCT test. The JASO-CCT test was carried out for 12 cycles according to JASO M 610-92. As a criterion for the JASO-CCT test, the rating number was determined by a method conforming to JIS G 0595: 2004, and "3" was used as the boundary value. Steel grades having a rating number of 4 to 9 were judged to have excellent corrosion resistance, and are indicated by reference numerals in Tables 2A and 2B. On the other hand, steel grades having a rating number of 0 to 3 were judged to be inferior in corrosion resistance, and are indicated by a symbol “x” in Tables 2A and 2B.

Further, in the vicinity of the center of the produced steel sheet in the width direction, the crystal orientation of the steel was analyzed by using an electron backscatter diffraction method (hereinafter, EBSD). The crystal orientation group that contributes to the magnetic characteristics is the crystal orientation divided into three regions at the center of the plate thickness: {100} ± 15 ° orientation grain, {110} ± 15 ° orientation grain, and {111} ± 15 ° orientation grain. The map was displayed and quantified. That is, on the surface parallel to the steel plate surface, EBSD was measured in the measurement region of 800 μm in the plate width direction and 2000 μm in the rolling direction at a magnification of 100 times, and the normal direction and the {100} plane direction of the surface parallel to the steel plate surface were measured. Crystal grains whose angle difference from the {110} plane orientation and the {111} plane orientation is within 15 ° (that is, {100} ± 15 ° orientation grains, {110} ± 15 ° orientation grains, {111} ± 15 ° orientation The crystal orientation map of the grain) was displayed, the area ratio was displayed, and the measurement was performed.

Furthermore, the following tests were conducted to evaluate the magnetic properties.
First, the temperature was raised in a vacuum of 1.3 × 10 ⁻² Pa at a heating rate of 1 to 100 ° C./min, magnetic annealing was performed at a magnetic annealing temperature of 950 ° C. for 2 hours, and then air cooling was performed.

A ring sample having an outer diameter of 45 mm, an inner diameter of 33 mm, and a height of 0.8 mm was cut out by electric discharge machining from the vicinity of the center in the width direction of the steel sheet after magnetic annealing. This ring sample was cured with a Kapton film, the secondary winding was wound for 100 turns, then stored in an acrylic case, and the primary winding was wound for 200 turns to obtain a ring-shaped test sample for direct current and AC magnetic measurement. .. Using this ring-shaped test sample, DC magnetic measurement and AC magnetic measurement were performed with a magnetic measuring device (BH analyzer SY-8258 manufactured by Iwadori Measurement Co., Ltd.).

As a DC magnetic measurement condition, the initial magnetization curve up to 4 kA / m is measured, and the relative magnetic permeability is calculated by the following equation (1). The maximum relative magnetic permeability μ _m , which is the maximum value, was determined.

μ _m = B / μ ₀ H ・ ・ ・ (1)
(B: magnetic flux density, μ ₀ : vacuum magnetic permeability (4π × ^10-7 H / m), H: magnetic field strength)

When the maximum relative magnetic permeability μ _m is 2800 or more, it is judged as acceptable (○) as having excellent magnetic characteristics in a DC magnetic field, and when the maximum relative magnetic permeability μ _m is less than 2800, it is judged as rejected (×). ..

As the AC magnetic measurement conditions, the magnetic field wave height value was 0.8 kA / m, and the measurement frequency was 1.0 kHz. When the maximum magnetic flux density was 0.80 T or more, it was judged to be acceptable (◯) as having excellent magnetic characteristics in an AC magnetic field. When the maximum magnetic flux density was less than 0.80 T, it was judged as rejected (x).

The results are shown in Table 2A and Table 2B.
When the composition and Si + Al ≥ 0.50 (Si and Al indicate the mass% concentration of each element) are satisfied and the area ratio of each crystal orientation is satisfied, the JASO-CCT test result and the DC magnetic field and the AC magnetic field are used. It can be seen that the magnetic characteristics pass (“○”).

In Comparative Examples B1 to B4, Si + Al ≧ 0.50 (Si and Al indicate the mass% concentration of each element) or Ni content was not satisfied, and the evaluation results were “x” in both corrosion resistance and magnetic properties. .. In particular, those not satisfying Si + Al did not satisfy the AC magnetic characteristics, and those not satisfying the Ni content did not satisfy the DC magnetic characteristics.

In Comparative Examples B5 to 8, since the annealing temperature of the hot-rolled plate annealing was low and the number of coarse grains was small, the area ratio of the {100} ± 15 ° oriented grains was less than 2.0%, and C / (A + B) ≤15. It did not satisfy 0, nor did it satisfy the magnetic characteristics of direct current. In B5, B7 and B8, since the accumulation of strain in the coarse grains was small, the area ratio of the {110} ± 15 ° oriented grains was also less than 2.0%.

In Comparative Examples B9 to 12, the annealing temperature of the cold-rolled plate annealing was high, so that the {111} ± 15 ° oriented grains grew significantly with respect to the {110} ± 15 ° oriented grains and the {100} ± 15 ° oriented grains. And did not satisfy C / (A + B) ≦ 15.0. Further, precipitates such as FeTiP that suppress the growth in the {111} plane orientation were coarsely precipitated. As a result, the growth of the {111} plane orientation could not be suppressed during magnetic annealing, and the magnetic characteristics of the DC magnetic field were not satisfied.
In Comparative Examples B13 to B13, since the rolling reduction during cold rolling was low, the recrystallization of {110} ± 15 ° oriented grains during cold rolling was insufficient, and the magnetic characteristics in the DC magnetic field were not satisfied.

Since the ferrite-based stainless steel of the present invention can achieve both corrosion resistance and magnetic properties in a DC magnetic field and an AC magnetic field, it can be used in motor cases such as stepping motors and hysteresis motors, motor parts such as motor cores, electronic throttle sensors and EPS sensors. It can be suitably used for such sensors, injectors, relays, electromagnetic valves, and their cores, yokes, connectors, housings, and the like. That is, the present invention is extremely useful industrially.

Claims (2)

By mass%
C: 0.001 to 0.030%,
Si: 0.01 to 3.00%,
Mn: 0.01-2.00%,
P: 0.030% or less,
S: 0.0050% or less,
Ni: 0.05 to 3.00%,
Cr: 5.0-18.0%,
Al: 0.001-5.000%,
V: 0.001 to 1.000%,
B: 0.0001 to 0.0100%, and N: 0.001 to 0.030%,
Further, it contains any one or two of Ti: 0.01 to 0.30% and Nb: 0.001 to 0.60%, the balance is Fe and impurities, and Si + Al ≧ 0.50 or more. Meet,
A ferritic stainless steel sheet characterized in that the texture on the plate surface satisfies the following (a) to (c).
(A) The angle difference between the normal direction of the steel plate surface and the {110} plane orientation on the plate surface is within 15 °, and the area ratio of the {110} ± 15 ° orientation grains is more than 2.0% and less than 20.0%. ..
(B) The angle difference between the normal direction of the steel plate surface and the {100} plane orientation on the plate surface is within 15 °. The area ratio of the {100} ± 15 ° orientation grains is more than 2.0% and less than 20.0%. ..
(C) On the plate surface, the area ratio of the {110} ± 15 ° orientation grains is A, the area ratio of the {100} ± 15 ° orientation grains is B, and the normal direction and {111} plane orientation of the steel plate surface on the plate surface. When the area ratio of the {111} ± 15 ° directional grain having an angle difference of 15 ° or less is C, C / (A + B) ≦ 15.0. Furthermore, instead of a part of Fe, by mass%,
Mo: 0.01-3.00%,
Sn: 0.001 to 3.00%,
Cu: 0.01-3.00%,
W: 0.001 to 1.00%,
Sb: 0.001 to 0.100%,
Co: 0.001 to 0.500%,
Ca: 0.0001 to 0.0050%,
Mg: 0.0001 to 0.0050%,
Zr: 0.0001 to 0.0300%,
Ga: 0.0001 to 0.0100%,
Ta: 0.001 to 0.050%,
REM: 0.001 to 0.100%
The ferritic stainless steel sheet according to claim 1, wherein one or more of the above-mentioned ferritic stainless steel sheets are contained.