JPH0641643A - Manufacture of ferritic alloy rolled stock - Google Patents

Abstract

PURPOSE:To easily manufacture the thin rolled stock of a Fe-Cr-Ni-Al ferritic alloy suitable for manufacturing the edge of an electric shaver or the like by a simple process. CONSTITUTION:The rolled stock of an Fe-Cr-Ni-Al ferritic alloy formed into a thin material by a rapid solidifying method is subjected to temp. treatment in such a manner that it is soaked at a temp. T1 in the range of 950 to 1200 deg.C, is gradually cooled to a temp. T2 in the range of 650 to 800 deg.C at a cooling rate alpha of 10 deg.C/min or lower and is thereafter rapidly cooled, which is then subjected to cold rolling and is again subjected to the same temp. treatment.

Description

Detailed Description of the Invention

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing a rolled ferrite alloy material suitable for producing a blade having both the hardness of ceramics and the strength of metal, particularly the inner and outer blades of an electric razor.

[0002]

2. Description of the Related Art A Fe-Cr-Ni-Al ferrite alloy has a high base metal hardness (Vickers hardness Hv: 400 or more because a NiAl metal compound having a diameter of several μm or less is dispersed and precipitated in the base metal. ), The surface hardness is 20 by thermal oxidation.
It can be enhanced by depositing an α-alumina layer within μm. If this Fe-Cr-Ni-Al ferrite alloy is used, it can be expected to realize the inner and outer blades of an electric razor having both the hardness of ceramics and the strength of metals.

However, since the Fe-Cr-Ni-Al ferrite alloy is a high hardness material, it lacks workability.
It is a difficult-to-process material. To make the inner and outer blades of a razor, it is necessary to make the alloy thin, but in ordinary cold rolling, the number of times of annealing must be extremely large, and since it can be processed only with a small rolling reduction. However, it is difficult to properly thin the material. Further, in the case of hot rolling or warm rolling, the yield is poor and the productivity is low, which is not suitable for practical use.
In particular, it is extremely difficult to reduce the thickness to about 30 to 40 μm, which is required for the outer blade of an electric razor.

Therefore, the inventors previously proposed the following method. A Fe-Cr-Ni-Al ferrite alloy material in a molten state is directly thinned by a rapid solidification method, and a blade is manufactured using the thin ribbon (Japanese Patent Laid-Open No. 3-153825). Although the rolling process can be greatly simplified, the ribbon produced by the rapid solidification method is not uniform in thickness. Therefore, cold rolling is also required to make the thickness uniform and to improve the rapidly solidified structure. However, after all, since the base material hardness is high and cracks occur in cold rolling, appropriate cold rolling is difficult.

[0005]

SUMMARY OF THE INVENTION In view of the above circumstances, the present invention is a thin Fe suitable for manufacturing a blade of an electric razor and the like.
An object of the present invention is to provide a method capable of easily producing a rolled material of a -Cr-Ni-Al ferrite alloy by a simple process.

[0006]

To achieve the above object, in the method for producing a rolled ferrite alloy material according to the present invention, Fe--Cr--N thinned by a rapid solidification method is used.
The i-Al ferrite alloy is soaked at a temperature in the range of 950 to 1200 ° C., then gradually cooled to a temperature in the range of 650 to 800 ° C. at a cooling rate of 10 ° C./minute or less, and then rapidly cooled. After the temperature treatment is performed and cold rolling is performed, the temperature treatment is performed again.

The present invention will be described more specifically below. The Fe-Cr-Ni-Al ferrite alloy (hereinafter referred to as "ferrite alloy") in the present invention is
As will be described later in detail, Cr: 20 to 40% by weight,
Ni: 10 to 25% by weight, Al: 4 to 8% by weight, Zr,
Any one or more of Y, Hf, Ce, La, Nd and Gd: 0 to 1.0% by weight, Ti, Nb
And any one or more of Mo: 0 to
It is preferable that the composition is 2% by weight and the balance is Fe.

In the case of the present invention, a ferrite alloy thinned by the rapid solidification method is used, which can be obtained as follows. First, a raw material metal having a composition suitable for a desired composition is placed in an alumina crucible, melted in a vacuum, and then cooled to obtain a mother alloy in advance. Then, the mother alloy is put into a nozzle made of quartz or carbon, and melted again in an inert atmosphere such as an argon atmosphere to obtain a melting point to a melting point +50.
Made of metal (cooling) in which molten metal in the temperature range of ℃ (50 ℃ above the melting point) is rotated from the nozzle by applying argon gas pressure
By jetting onto a roll, it is rapidly solidified to obtain a ribbon continuously. This ribbon is a ferrite alloy that is made thinner.

The rapid solidification method includes a single roll method and a twin roll method. In the case of the single roll method, for example, diameter 300 mm
Only one copper roll is used, a ribbon with an average thickness of about 40 μm is obtained when the peripheral speed of the roll is 30 m / sec, and an average thickness of about 40 μm is obtained when the peripheral speed of the roll is 10 m / sec. A ribbon of 100 μm is obtained. Usually, average thickness 30 ~
It is possible to obtain a film having a width of about 50 mm and a length of about 20 m and a length of about 150 μm. The nozzle at this time is, for example, made of carbon and has a tip with a width of 0.5 mm and a length of 5 mm.
A nozzle provided with a 0 mm slit is exemplified. The distance between the surface of the roll and the tip of the nozzle is usually set to about 1 mm, for example.

In the case of the twin roll method, for example, the diameter is 100 m.
Two copper m rolls are arranged to face each other, and the rolls are rotated in synchronism with the molten metal injection performed from the nozzle tip arranged 20 to 30 mm above the gap between the rolls so as to be rapidly cooled and solidified under the pressure of the rolls. . Roll speed 30m /
When it is set to seconds, a ribbon having an average thickness of about 80 μm is obtained, and when the peripheral speed of the roll is set to 10 m / sec, an average thickness of about 200 μm is obtained.
A strip of m is obtained. The nozzle at this time is, for example, made of carbon and has a tip with a width of 1 mm and a length of 20 mm.
The nozzle provided with the slit is illustrated. The width of the obtained ribbon depends on the peripheral speed of the roll. The higher the peripheral speed, the narrower the width. For example, when the peripheral speed is 10 m / sec, a ribbon having a width of about 25 mm is obtained. Average thickness 8
A product having a length of about 0 to 250 μm and a length of about 40 m can be obtained.

On the surface of the obtained ribbon, wrinkles are usually observed. The fluctuations of the plate thickness in the width direction and the length direction are ± 20% (width direction) and ± 40% for a single roll
(Longitudinal direction), and were ± 10% (width direction) and ± 30% (longitudinal direction) in the case of twin rolls. But usually,
No fatal defects such as surface cracks and holes are observed on the surface of the ribbon.

The thus obtained thin ferrite alloy obtained by the rapid solidification method is subjected to the following heat treatment before cold rolling. This heat treatment is also performed after cold rolling. The thin ferrite alloy obtained by the rapid solidification method is brittle and very hard, and cold rolling does not work as it is. In other words, this thinned ferrite alloy is extremely brittle because the dendrites grown inward from the rapidly solidified surface occupy a large volume ratio, and
The freeze-dispersed fine NiAl grains have a high hardness of 600 or more. Therefore, it is annealed in advance by heat treatment.

Further, the heat treatment after the cold rolling has the disadvantages caused by this rolling work, namely, relaxation of work strain of ferrite crystal grains, relaxation of anisotropy of fine ferrite crystal grains, and anisotropy of NiAl grains. Relaxation and particle shaping (adjusting the shape and size), and further, ferrite crystal grains and NiA
This is done for the purpose of relaxation of strain at the interface of 1 grain. First, 9
Soaking is performed at a temperature of 50 to 1200 ° C. The soaking treatment referred to in the present invention is a heat treatment carried out in the same temperature state for the entire thin ferrite alloy to be treated (surface and inside). Of course, since the ferrite alloy is thin, even if nothing special is done, the whole is quickly brought to the same temperature by the ordinary heat treatment.

In the soaking treatment before cold rolling, fine NiAl
Grain coarsening progresses. That is, fine NiAl grows and becomes coarse. However, when the soaking temperature exceeds 1200 ° C, the NiAl grains, which improve hardness, rapidly disappear as a solid solution in the base material, and coarsening of ferrite crystal grains cannot be suppressed, and the temperature is lowered to 1200 ° C or less. NiA along with
Although l is re-precipitated, NiAl is also precipitated at the ferrite grain boundaries at this time, resulting in embrittlement of the alloy.

In the soaking treatment after cold rolling, 950
When the temperature is higher than ℃, the NiAl grains stretched by cold rolling and deformed into linear or flat plate become coarse due to solid solution / reprecipitation and change into round bar or sphere. Sexuality is eased. In addition, as the atomic diffusion occurs between the ferrite crystal grains and the NiAl grains, the strain at the interface between the grains is relaxed. Also, NiAl
At the same time as the anisotropy of the grains is relaxed, the strain and anisotropy of the ferrite crystal grains themselves are also relaxed. The defects of the work structure that have occurred in the structure during cold rolling are eliminated. 1200 ° C
The inconvenience when passing over is the same as above.

In the case of soaking at a temperature of 950 to 1200 ° C., the temperature is not higher than the complete solution temperature, but it is thermally activated due to the high temperature, and NiAl violates solid solution / reprecipitation in the ferrite matrix phase. Is repeating. Although the solid solution rate / reprecipitation rate of NiAl is a function of temperature, the precipitation rate is larger, and NiAl grains having a certain size from the beginning become coarse (average particle size of several μm). On the other hand, although nucleation of new NiAl grains is occurring in the ferrite matrix phase, the NiAl nuclei having a small grain size are unstable at a high temperature and cannot grow large. While suppressing the increase in hardness,
Therefore, it becomes possible to eliminate defects in the processing structure.

The time required for soaking is longer as the temperature is lower. At 1200 ° C., when the temperature of the ferrite alloy reaches that temperature, it is sufficient to move to the next gradual cooling, and 30 minutes is the upper limit of the treatment time. 5 minutes to 2.5 hours at 1100 ° C., 1
It is 15 minutes or more and 10 hours or less at 000 ° C. It is better to lengthen the soaking time at low temperature and shorten the soaking time at high temperature. If the soaking time is low at a low temperature, defects in the work structure cannot be resolved, and the alloy hardness will not decrease. If the soaking time at a high temperature is too long, NiAl grains and ferrite crystal grains are coarsened, and alloy embrittlement occurs, which easily causes cracking during processing.

After soaking at 950 to 1200 ° C., the temperature is lowered, but it is not cooled as it is, but is gradually cooled to a temperature of 650 to 800 ° C., usually 650
Soaking is performed at a temperature of ~ 800 ° C. At this time, 950
65 from a temperature of 1200 ° C at a cooling rate of 10 ° C / min or less
Gradually cool to a temperature of 0 to 800 ° C. This is because the hardness of the alloy does not become sufficiently low when the temperature is lowered at a cooling rate higher than this. That is, 950 to 1200 ° C to 650 to 800
Comparing the temperature decrease to ℃ with slow cooling at a cooling rate of 10 ° C./min or less and with rapid cooling at a cooling rate of more than 10 ° C./min, the former shows that NiAl grains of 1 μm or less are produced. As a result, the required hardness can be reduced. This is because N having a particle size of 1 μm or less is gradually cooled during slow cooling.
iAl grains grow larger, and as a result, finer NiAl
It is speculated that this is because the generation of grains is hindered. Usually, a cooling rate of about 5 to 8 ° C / minute is preferable. The lower the cooling rate, the greater the decrease in hardness, but at about 1 ° C./minute, the effect of decreasing the hardness becomes saturated and energy is wasted. .

The temperature range of 650 to 800 ° C. is
This is because if the temperature is lower than 650 ° C, the alloy becomes brittle.
This is because if the temperature exceeds 00 ° C, the effect of decreasing the hardness does not sufficiently appear. In terms of ensuring sufficient reduction of alloy hardness, 6
It is preferably in the range of 50 to 750 ° C. The treatment time for soaking is within 1 hour. By this soaking treatment, the amount of fine NiAl grains is reduced, and sufficient hardness reduction can be achieved. The effect of soaking is 1 treatment time
Even if saturation is reached in time and further processing is not expected, the effect cannot be expected to increase, and the amount of energy consumed only increases, so the processing time is set to 1 hour or less.

Then, rapid cooling is performed. Fe-
It rapidly passes through the embrittlement temperature range (about 400 to 600 ° C.) of the Cr—Ni—Al ferrite alloy, and causes σ embrittlement and 475.
Do not allow embrittlement at ° C. As the rapid cooling method, normal air cooling that is left in a room temperature atmosphere, forced air cooling using a fan or a blower, or the like is used. Water cooling is not recommended because it may cause thermal stress cracking.

The thin ferrite alloy thus heat-treated is cold-rolled before cold rolling. Cold rolling is usually performed so that the thickness after rolling is about 45 to 95, where the thickness before rolling is 100. In addition, after rolling, post-processing is performed to form a shape suitable for the blade of the electric razor. In addition, a ferrite alloy prepared in a predetermined shape by post-processing is usually used in an oxidizing atmosphere at 1100 to 13
Heat treatment is performed at about 50 ° C. to form an α-alumina film. After forming the alumina coating, the alloy hardness is increased by rapid cooling or the like.

Then, Fe-Cr-Ni- which is a raw material
Regarding the elements contained in the Al-based ferrite alloy, the reasons for limiting the content will be described. The alloy of the present invention is a Fe-based alloy containing a large amount of ferrite-forming elements Cr and Al and austenite-forming element Ni, and the reason why the alloy is mainly in the ferrite phase is as follows. Ferrite phase alloys tend to form a dense alumina (Al ₂ O ₃ ) film that is dense and has good adhesion to the substrate by oxidation heat treatment, but austenite phase alloys do not form an alumina film uniformly and peel off. Because.

[Cr: 20-40 wt%] Cr is necessary for forming a dense and uniform alumina film on the alloy surface, but since the alloy of the present invention contains Ni,
In order to make the alloy into a ferrite phase, Ni is the lower limit value of A
Even when 1 is the upper limit value, 25 wt% or more of Cr is required. Ni content is lower limit, Al content is near upper limit, Cr content is 2
If the alloy content is less than 5% by weight, the formation of alumina film is incomplete. Therefore, the lower limit of Cr is 25 wt%. Further, as the Cr content in the alloy increases, the tendency of embrittlement increases, so the upper limit of Cr is 40 wt%.

[Ni: 10 to 25 wt%] Ni is presumed to precipitate fine NiAl in the alloy and improve the mechanical properties (eg hardness) of the base material. Is an essential element for precipitating NiAl. 15 to be effective enough to improve mechanical properties
Requires more than wt% Ni. If the amount of Ni increases, N
Although it is convenient for the precipitation of iAl, if the content of Ni which is an austenite forming element is increased, C
It is necessary to increase the content of r and Al. However, if the Ni content exceeds 25 wt%, the Cr content must be increased, and if this is the case, embrittlement easily occurs, so the upper limit of Ni is 25 wt%.

[Al: 4-8 wt%] Al is a fine N
It is an essential element for precipitating iAl in the alloy and for forming an alumina film on the alloy surface by high temperature oxidation treatment. In order to form a dense and uniform film,
It is necessary to contain 4 wt% or more of Al. An increase in the Al content is advantageous for the precipitation of NiAl and the formation of an alumina film, but if it exceeds 8 wt%, the workability of the alloy decreases, so the upper limit of Al is 8 wt%.

[One or more of Zr, Y, Hf, Ce, La, Nd and Gd: 0 to 1.
0% by weight] Each of these elements is added as necessary, and is mixed into the aluminum film to improve the brittleness of the film and to be dispersed as internal oxide particles in the alloy immediately below the film to form a film. Remarkably improves the adhesion. In order to exert these effects, it is preferable to contain 0.05 wt% or more. On the other hand, if the content exceeds 1% by weight, the workability of the alloy sharply deteriorates, so the upper limit is 1% by weight.

[One or Two or More of Ti, Nb and Mo: 0 to 2.0% by Weight] Each of these elements is also added as necessary and is mixed in the aluminum film. Thus, the brittleness of the coating is improved, and the particles are dispersed as internal oxide particles in the alloy immediately below the coating, and the adhesion of the coating is significantly improved. However, 2% by weight
If it is contained in an amount exceeding the above range, the alloy characteristics will be deteriorated, so the upper limit is limited to 2% by weight.

[Fe: Remainder] In addition to the above components, Fe occupies. However, it is not limited to the case where the balance is completely Fe, and there may be inevitable impurities (such as Si) present in Fe. The applications of the rolled ferrite alloy obtained by the method of the present invention include inner blades and outer blades of electric razors that require abrasion resistance and corrosion resistance, but are not limited to these. Needless to say.

[0029]

In the present invention, the ferrite alloy formed by thinning by the rapid solidification method is used.
Unlike the conventional case of annealing and thinning the material, only two annealings and one rolling are required, so the process is very simple. In addition, in the case of the present invention, appropriate annealing is performed by heat treatment under appropriate conditions before cold rolling, and cracks and the like do not occur in cold rolling, so that manufacturing is very easy.

Of course, in the case of the present invention, appropriate annealing is performed by heat treatment under appropriate conditions even after cold rolling,
The rolled material thus obtained is suitable for manufacturing an electric razor blade or the like, which can be processed into a required shape without any trouble.

[0031]

Embodiments of the present invention will be described below. It goes without saying that the present invention is not limited to the following embodiments.
In the examples, columnar ingot alloys 1 and 2 having the following compositions were used as mother alloys. [Alloy 1] Cr: 26.0 wt% Ni: 15.0 wt% Al: 4.5 wt% Zr: 0.2 wt% Y: 0.6 wt% Ti:
0.5 wt% balance: Fe [alloy 2] Cr: 35.0 wt% Ni: 21.0 wt% Al: 7.0 wt% Zr: 0.3 wt% Nb: 1.0 wt% balance: F
e -Examples 1 to 10-The melt of Alloy 1 was rapidly solidified by the single roll method and the twin roll method to obtain a thin strip (thin material).

In the case of the single roll method, a nozzle made of carbon and having a slit with a width of 0.5 mm and a length of 50 mm is provided while rotating a copper roll having a diameter of 300 mm at a peripheral speed of 20 m / sec. Was placed at a distance of 1 mm from the surface of the roll, and the molten metal of Alloy 1 having a melting point to a melting point of + 50 ° C. was discharged at an argon gas pressure. The obtained ribbon has an average thickness of 60 μm, a plate width of 45 mm, and a length of 20 m.
It was a continuous belt. The variation in plate thickness was 40 to 80 μm.

In the case of the twin roll method, while rotating a copper roll having a diameter of 100 mm at a peripheral speed of 20 m / sec, a nozzle made of carbon and provided with a slit having a width of 1 mm and a length of 20 mm at the tip, A molten metal of alloy 1 having a melting point to a melting point + 50 ° C. was discharged at an argon gas pressure.
The obtained ribbon has an average thickness of 150 μm and a plate width of 20 m.
It was a continuous zone of m and 40 m in length. Variation in plate thickness is 11
It was 0 to 180 μm.

No noticeable surface cracks or defects such as holes were observed in the obtained ribbon. The hardness of the obtained ribbon was HV = 600. These ribbons were subjected to a heat treatment through the temperature change shown in FIG. 1 under the specific conditions shown in Table 1. The temperatures T1, T2, t1 in FIG. 1 and Table 1 are as follows. Note that the heat treatment was performed in an argon atmosphere to prevent oxidation.

T1: soaking temperature at 950 to 1200 ° C t1: soaking time at 950 to 1200 ° C α: cooling rate from 950 to 1200 ° C to 650 to 800 ° C T2: rapid cooling start temperature Cold-rolled to a thickness of 37μ
m and 100 μm. The average hardness after rolling is Hv: 40
It was over zero. After rolling, the same heat treatment as described above was performed again to obtain a rolled ferrite alloy material. Table 2 shows the hardness of the ribbon after heat treatment, the presence or absence of cracks in cold rolling, and the hardness after heat treatment after cold rolling.

Among the obtained rolled ferrite alloys, those having a thickness of 37 μm were in the form of outer blades of an electric razor,
When the thickness of 100 μm was punched by using an inner blade of an electric razor, no cracks were found.

[0037]

[Table 1]

[0038]

[Table 2]

-Comparative Examples 1 to 6-The strips having a thickness of 150 μm obtained in Examples 1 to 10 were subjected to a temperature treatment under conditions (Table 3) which deviate from the temperature treatment conditions of the present invention, and cold rolling was performed. gave. Table 4 shows the observation results of hardness after heat treatment and presence or absence of cracks during cold rolling. In Comparative Examples 1 to 6, it was found that all cracks occur during the rolling process.

[0040]

[Table 3]

[0041]

[Table 4]

-Examples 11 to 20-The melt of Alloy 2 was rapidly solidified by the single roll method and the twin roll method to obtain a thin strip (thin material). In the case of the single roll method, a copper roll having a diameter of 300 mm is rotated at a peripheral speed of 20 m / sec while being made of carbon and having a width of 0.
A nozzle provided with a slit having a length of 5 mm and a length of 50 mm is installed at a distance of 1 mm from the roll surface, and the melting point to the melting point +
The molten alloy 2 at 50 ° C. was discharged at an argon gas pressure. The obtained thin strip was a continuous strip having an average thickness of 60 μm, a plate width of 45 mm and a length of 20 m. The variation in plate thickness was 40 to 80 μm.

In the case of the twin roll method, while rotating a copper roll having a diameter of 100 mm at a peripheral speed of 20 m / sec, a nozzle made of carbon and provided with a slit having a width of 1 mm and a length of 20 mm at the tip, A melt of alloy 2 having a melting point to a melting point + 50 ° C. was discharged at an argon gas pressure.
The obtained ribbon has an average thickness of 150 μm and a plate width of 20 m.
It was a continuous zone of m and 40 m in length. Variation in plate thickness is 11
It was 0 to 180 μm.

No noticeable defects such as surface cracks and holes were observed in the obtained ribbon. The hardness of the obtained ribbon was HV = 660. These ribbons were subjected to a heat treatment through the temperature change shown in FIG. 1 under the specific conditions shown in Table 5. After heat treatment, cold strip the ribbon,
The thickness was 37 μm and 100 μm, respectively. The average hardness after rolling exceeded Hv: 450. After rolling
Again, the same heat treatment as above was applied to obtain a rolled ferrite alloy material. Table 6 shows the hardness of the thin strip after heat treatment, the presence or absence of cracks in cold rolling, and the hardness after heat treatment after cold rolling.

Among the obtained rolled ferrite alloys, those with a thickness of 37 μm were in the shape of the outer blade of an electric razor,
When the thickness of 100 μm was punched by using an inner blade of an electric razor, no cracks were found.

[0046]

[Table 5]

[0047]

[Table 6]

-Comparative Examples 7 to 12-The thin strips having a thickness of 60 μm obtained in Examples 11 to 20 were subjected to a temperature treatment under conditions deviating from the temperature treatment conditions of the present invention (Table 7), followed by cold rolling. gave. Table 8 shows the hardness after heat treatment and the results of observation of the presence or absence of cracks during cold rolling. In Comparative Examples 7 to 12, it was found that all cracks were generated during the rolling process.

[0049]

[Table 7]

[0050]

[Table 8]

From the results of investigations on the presence or absence of cracks in Examples and Comparative Examples, it can be clearly seen that in the case of the present invention, annealing is appropriately performed by heat treatment.

[0052]

In the method for producing a rolled ferrite alloy material according to the present invention, the ferrite alloy thinned by the rapid solidification method is used, and it can be annealed twice and rolled once. In addition to the simple process, appropriate annealing has been performed, and cold rolling can be performed without any problems, so it is very easy to manufacture, and furthermore, appropriate annealing is performed even after cold rolling, Good post-processability makes it suitable for manufacturing electric razor blades.

[Brief description of drawings]

FIG. 1 is a graph showing the relationship between the treatment time and the treatment temperature in the heat treatment of the present invention.

[Explanation of symbols]

T1: soaking temperature at 950 to 1200 ° C t1: soaking time at 950 to 1200 ° C α: cooling rate from 950 to 1200 ° C to 650 to 800 ° C T2: quenching start temperature

─────────────────────────────────────────────────── ─── Continuation of the front page (51) Int.Cl. ⁵ Identification code Office reference number FI technical display location C22C 38/40 38/50

Claims (2)

[Claims] 1. Fe-formed by thinning by a rapid solidification method
Cr-Ni-Al ferrite alloy, 950-120
After soaking at a temperature in the range of 0 ° C., the temperature is gradually cooled to a temperature in the range of 650 to 800 ° C. at a cooling rate of 10 ° C./minute or less, and then rapidly cooled. A method for producing a rolled ferrite alloy material, which comprises rolling and then performing the temperature treatment again. 2. An Fe-Cr-Ni-Al ferrite alloy comprising Cr: 20 to 40% by weight, Ni: 10 to 25% by weight, Al: 4 to 8% by weight, Zr, Y, Hf, Ce, L.
Any one or more of a, Nd and Gd: 0 to 1.0% by weight, any one or more of Ti, Nb and Mo: 0 to 2% by weight, and the balance: F
The method for producing a rolled ferrite alloy material according to claim 1, which has a composition of e.