JPH02243745A - Magnet alloy and its manufacture - Google Patents

Abstract

PURPOSE:To surely manufacture the magnet alloy of stable quality having excellent magnetic characteristics in the direction parallel to rolling by casting an Fe-Cr-Co series alloy having specified compsn., subjecting it to hot rolling and thereafter repeatedly executing recrystallization annealing with cold rolling obviated. CONSTITUTION:The molten metal of an alloy contg., by weight, 10 to 40% Cr, 3 to 30% Co and the balance Fe is cast and is thereafter subjected to hot rolling in the temp. range of [the temp. at which an alpha phase exists by 50% in an (alpha+gamma) phase + 50 deg.C] or above to [the m.p. - 50 deg.C] or below. The alloy is successively subjected to primary recrystallization annealing in the (alpha+gamma) phase area and is furthermore subjected to secondary recrystallization annealing to manufacture the above magnet alloy. After the above hot rolling, if required, the alloy is successively subjected to primary recrystallization annealing in the single phase area of an alpha phase, is thereafter to heating treatment in the (alpha+gamma) area, is furthermore to heating treatment in the (alpha+gamma+sigma) phase area and is thereafter to secondary recrystallization annealing.

Description

DETAILED DESCRIPTION OF THE INVENTION Field of Industrial Application This invention relates to F, which is known as a magnetic alloy exhibiting magnetic anisotropy.
The present invention is directed to an e-Cr-Co magnet alloy and a method for manufacturing the same.

BACKGROUND OF THE INVENTION In recent years, Fe--CrCo-based magnet alloys have been developed which provide magnetic anisotropy through spinodal decomposition in a magnetic field. This magnet alloy generally has Cr10-40
%, about 3 to 30% Co, with the balance mainly consisting of Fe, and is solution treated at high temperature 3JJ.
! After that, heat treatment in a magnetic field such as isothermal magnetic field treatment or cooling in a magnetic field is added to perform so-called spinodal decomposition, which causes single-domain fine particles of the ferromagnetic phase to precipitate with shape anisotropy in the non-magnetic matrix phase, resulting in magnetic anisotropy. It can give direction. This Fe-Cr-Co magnetic alloy is
Unlike ferrite magnets, etc., it can be rolled, so it is expected to be used for a variety of purposes.

However, it is actually difficult to give the above-mentioned Fe-Cr-Co-based magnet alloy such high magnetic properties just by spinodal decomposition through heat treatment in a magnetic field, and therefore it is difficult to improve its magnetic properties beyond a certain level. Met.

Therefore, the present inventors have already published Japanese Patent Application No. 55-64497 (
Japanese Patent Application Laid-Open No. 163218/1982) and Japanese Patent Application No. 1983/1983. -7
In No. 4745 (Unexamined Japanese Patent Publication No. 56-169722),
Inspired by the method for producing grain-oriented silicon steel sheets, we have proposed a method for producing a FeCr-Co magnetic alloy having a texture in which the crystal's easy axis of magnetization, that is, the <100> axis, is aligned in the rolling direction. These proposed methods use /MN or MnS as an inhibitor to the growth of primary recrystallized grains during high-temperature annealing after cold rolling, and thereby prevent the growth of primary recrystallized grains ( 100> Secondary recrystallized grains with axes oriented are generated, and the (100
>The aim is to obtain a magnetic material having a texture with aligned axes. It is thought that by further processing the magnetic material obtained in this manner by applying a magnetic field in the rolling direction, a magnet having excellent magnetic properties in the rolling direction can be obtained.

Although it is recognized that each of the above-mentioned proposed methods is certainly effective to some extent in improving magnetic anisotropy, in reality, the <100> axis, which is the axis of easy magnetization of the crystal, is not necessarily aligned in the rolling direction. The reality is that there are cases where they are not sufficiently aligned, and as a result, there is a limit to the improvement of magnetic properties.

On the other hand, the inventors of the present invention have already disclosed in Japanese Patent Application No. 62-231495 that in manufacturing a Fe-Cr-Co magnet alloy, after casting a molten alloy, appropriate hot working is carried out, and then 5.0 to 99. Cold rolling is performed at a reduction rate within the range of 5%, followed by primary recrystallization annealing in the (α + γ) phase region,
Furthermore, a method of performing secondary recrystallization annealing is proposed. According to this method, the primary recrystallization annealing after cold rolling is performed by (α+
By performing this in the γ) phase region, that is, by forming an (α+γ) mixed phase structure and then performing secondary recrystallization annealing, the <100> axis is oriented perpendicular to the rolling direction during secondary recrystallization. It is possible to generate secondary recrystallized grains,
Moreover, in this case, the degree of orientation of the (100> axis in the direction perpendicular to the rolling direction in the secondary recrystallized structure is extremely high, and therefore it is possible to obtain a magnet with extremely excellent magnetic properties in the direction perpendicular to the rolling direction. can.

Problems to be Solved by the Invention According to the method of the above-mentioned Japanese Patent Application No. 62-231495, it is possible to obtain a magnet with extremely excellent magnetic properties in the direction perpendicular to the rolling direction, but the cold rolling process This requires a large number of steps and increases manufacturing costs. Furthermore, in practice, there is a problem in that the magnetic properties finally obtained vary considerably depending on the conditions of the cold rolling process. Furthermore, the magnetic properties in the direction perpendicular to the rolling direction are excellent, and the magnetic properties in the direction parallel to the rolling direction are low.
There were some problems that made it difficult to use depending on the purpose.

This invention was made against the background of the above-mentioned circumstances, and it is possible to reduce the cost by omitting the cold rolling process, and to obtain Fe, which has extremely excellent magnetic properties in the direction parallel to the rolling direction.
The object of the present invention is to provide a -Cr-Co based magnet alloy and a method for producing the same.

Means for Solving the Problems In order to solve the above-mentioned problems, the present inventors developed FeCr-C
After conducting various experiments and studies on the manufacturing method of o-based magnetic alloys, we found that the α-phase single-phase region or the (α+γ)-phase two-phase region in which the α phase exists in 50% or more, more precisely ((α
+γ) Temperature at which 50% α phase exists in the phase +50°C}~C
By performing hot rolling in the temperature range of (melting point -50°C) and then performing heat treatment in the (α + γ) phase region without performing cold rolling, the average grain size can be reduced by subsequent secondary recrystallization annealing. 2. It is possible to generate a secondary recrystallized structure in which the <100> axis is oriented in the direction parallel to the rolling direction, that is, the (110} <100> axis is parallel to the rolling direction.
In this case, by setting the average grain size to 2.0 ttrtnJJ or more as described above, the degree of accumulation in the direction parallel to the rolling direction of the (110) (100> axis becomes significantly higher). They discovered that it has excellent magnetic anisotropy, and came up with this invention.

Therefore, the magnetic alloy of the invention of claim 1 of the present application is Cr
In a Fe-Cr-Co magnet alloy containing 10 to 40% of Co and 3 to 30% of Co, with the balance mainly consisting of Fe, the average crystal grain size is 2.0. m or more and has a texture in which (110) (100> axes are oriented in a direction parallel to the rolling direction).

Further, the inventions of claims 2 to 5 each relate to a method of manufacturing the Fe-Cr-Co-based magnetic alloy of the invention of claim 1, and the manufacturing method of the invention of claim 2 includes Cr1
0 to 40% and 003 to 30%, with the remainder being Fe.
In producing a Fe-CrGO magnetic alloy mainly composed of
Hot rolling is performed at a temperature within the range of 0% existing temperature + 50 ° C} or higher and (melting point - 50 ° C} or lower, followed by (α + γ)
It is characterized in that primary recrystallization annealing is performed in the phase region, and then secondary recrystallization annealing is performed.

Further, in the manufacturing method of the invention of claim 3, after hot rolling similar to the above, primary recrystallization annealing is performed in a single phase region of α phase, and then (α
This secondary recrystallization annealing is performed by performing heat treatment in the +γ) phase region.

Furthermore, in the manufacturing method of the invention of claim 4, after hot rolling as described above, primary recrystallization annealing is performed in the (α+γ) phase region, and then (α
After heat treatment in the ``-γ1σ) phase region, secondary recrystallization annealing is performed.

Furthermore, the manufacturing method of the invention of claim 5 is a combination of the manufacturing method of the invention of claim 3 and the manufacturing method of the invention of claim 4, in which after the same hot rolling as described above, first the α phase single phase region is First recrystallization annealing is performed, then heat treatment is performed in the (α + γ) phase region, heat treatment is roughly performed in the (α1γ1σ) phase region, and then secondary recrystallization annealing is performed. It is something.

Function The magnetic alloy of the invention of claim 1 has an average crystal grain size of 2.01.
11#1 or more and has an easy axis of magnetization in the direction parallel to the rolling direction (1101 (100>) is said to have a set of 11 weaves with the axis oriented in the direction parallel to the rolling direction. By performing heat treatment in a magnetic field while applying a magnetic field in a direction parallel to the rolling direction, it is possible to obtain a magnet that has extremely high magnetic anisotropy in the direction parallel to the rolling direction and extremely high magnetic properties in that direction.

Here, if the average grain size is less than 2.01lI#I, even if heat treatment is performed in a magnetic field after solution treatment as described above, a texture with the (110}<100> axis oriented in the direction parallel to the rolling direction will be formed. The degree of integration is low, and therefore a magnet with sufficient magnetic properties in the direction parallel to the rolling direction cannot be obtained, and therefore it is necessary to have an average crystal grain size of 2.0 mm or more.

The magnet of the invention of claim 1 as described above can basically be manufactured by the manufacturing method of the invention of claim 2. That is, after melting and casting a molten alloy having the required composition, and subjecting it to hot casting as necessary, ((
The strain necessary for recrystallization is introduced by hot rolling in a temperature range from 50% of the α phase in the α+γ) phase to +50°C} and below the melting point of −50°C, and then (α+γ) Primary recrystallization annealing is performed in the two-phase region, and then secondary recrystallization annealing is performed.

Here, hot rolling needs to be carried out at a temperature in a region where 50% or more of the α phase exists in the α phase single phase or (α + γ) phase two phases, but in actual operation, the precipitation of the γ phase should be less than 50%. In order to reliably suppress local melting due to overheating while reliably suppressing the
It was decided to carry out hot rolling in a temperature range from the temperature at which 50% of the α phase exists in the α phase (+50°C) to (the melting point -50°C}).
Hot rolling in a region where α phase exists in 50% or more of the two γ) phases means that a (110) (100> texture in the direction parallel to the rolling direction is obtained by subsequent secondary recrystallization annealing. Therefore, unless rolling is performed in a region where α phase exists in a single phase or α phase (α + γ) two phases, 50% or more of the α phase exists.
It is not possible to obtain a (110}
After introducing a certain amount of strain by hot rolling in the region covered by 50% or more of the α phase among the two γ) phases, crystal annealing may be performed in the two-phase region of the (α+γ) phase. This is important, and by performing primary recrystallization annealing in the (α + γ) phase region in this way, an (α + γ) mixed phase structure is obtained as the primary recrystallization structure, and secondary recrystallization annealing is performed on this mixed phase structure. In some cases, the average grain size is set to 2.0w or more, and the rolling direction is parallel to the rolling direction (110}<100>
It becomes possible to obtain a material with a high degree of accumulation of texture with oriented axes.

As described above, in the direction parallel to the rolling direction (110}<
The reason why the set 1IIIIIIli in which the 100> axis is oriented is not yet clear, but it is generally thought to be as follows. In other words, in a single α phase or two (α+γ) phases,
(α
In the primary recrystallization annealing in the +γ) phase region, the γ phase mainly precipitates at the grain boundaries of the primary recrystallized grains. During secondary recrystallization annealing, the γ phase precipitated at this grain boundary becomes parallel to the rolling direction (1
It is thought that this contributes to the preferential growth of crystal grains with the 00> axis oriented.

In the case of the method of the invention of the earlier patent application No. 62-231495, cold rolling is performed after hot rolling, and then primary recrystallization annealing in the α+γ) phase region as described above and the subsequent two steps are performed. Next recrystallization annealing is performed, and in this case a texture with <100> axes oriented in a direction perpendicular to the rolling direction is obtained. On the other hand, in the present invention, a texture in which the <ioo> axis is oriented in a direction parallel to the rolling direction is obtained by omitting cold rolling and performing the same heat treatment, but this difference between the previous application and this invention is that This is thought to be due to the difference in the rolling process. That is, during hot rolling, the <100> axis is parallel to the rolling direction, but if rough cold rolling is performed, the <100> axis is considered to rotate in a direction perpendicular to the rolling direction.

In the manufacturing method of the invention of claim 3, after hot rolling in a region where 50% or more of the α phase is present in the above-mentioned single α phase or α + γ) phase, in the single α phase region. After primary recrystallization annealing is performed, heat treatment in the (α+γ) phase region is performed. In this case, the primary recrystallization is carried out as a single α phase, and the subsequent heating in the (α→−γ) phase region precipitates the γ phase at the primary recrystallized grain boundaries, and the γ phase precipitates at the grain boundaries. However, as in the case described above, during secondary recrystallization annealing, the secondary recrystallized grains whose (110) (100> axis is oriented in the direction parallel to the rolling direction) contribute to preferential growth. In the method of the invention, primary recrystallization is performed in the α phase before the (α+γ) phase is formed, so the structure is homogenized and the subsequent (
When the α+γ) phase is formed, the γ phase easily breaks at the grain boundaries, and as a result, it becomes easier to obtain a structure in which the (110}<100> axis is oriented in the direction parallel to the rolling direction.

In the manufacturing method of the invention of claim 4, in the α phase single phase or (α + γ) phase two phases, α
After hot rolling in the region where 50% or more of the phase exists (α + γ
After primary recrystallization annealing is performed in the 5-phase region, heating is performed to the temperature of the 3-phase region (α+γ+σ) at a stage before secondary recrystallization annealing is performed.

This precipitates the α phase, and the precipitation of the α phase introduces strain, and as a result, secondary recrystallization is more likely to occur during secondary recrystallization annealing, and the magnetic properties can be further improved.

The manufacturing method of the invention of claim 5 is a combination of the manufacturing method of the invention of claim 3 and the manufacturing method of the invention of claim 4, that is, the α phase accounts for 50% of the α phase single phase or (α+γ) two phases. After hot rolling in the region where the above exists, 1 in the α phase single phase region
Next, recrystallization annealing is performed to homogenize the matrix, followed by heating to the (α+γ) phase region to precipitate the γ phase at grain boundaries, and further heating to the (α+γ''-σ) phase region to precipitate the α phase. Introducing distortion by In this case, high magnetic properties can be obtained most effectively.

DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS First, the composition of the alloy targeted by the present invention will be explained.

The Fe-Cr-Co alloy targeted by this invention is basically mainly composed of 10 to 40% Cr, 003 to 30%, and the balance is Fe, but more preferably 20 to 3% Cr.
It is appropriate that the main content is 5%, 0.010 to 20%, and the balance Fe. Also, among these ingredients, F
A part of e may be replaced with 28% or less of MO. Furthermore, if necessary, W of 4% or less, ■i of 3% or less, 2%
It may contain one or more selected from the following Nb, 4% or less of V, and 2% or less of Zr.

Furthermore, the alloy targeted by this optical cutting suppresses the growth of primary recrystallized grains during secondary recrystallization annealing, resulting in (110)
In order to make MnS act as an inhibitor to preferentially generate secondary recrystallized grains whose <100> axes are parallel to the rolling direction, Mn 0101~2% and 3o, ooi~
1.0% may be included.

Here, if Mn is less than 0.01% or so, ooi% is not swirled, a sufficient amount of MnS cannot be generated, and therefore the inhibitor cannot have the effect of suppressing the growth of primary recrystallized grains, and Mn exceeds 2% or S is 1
．． If it exceeds 0%, the residual magnetic flux density of the finally obtained magnet alloy will decrease.

In addition, in order to cause AlN to act as an inhibitor to the growth of primary recrystallized grains as described above, Al2O,01~2
% and NO,0006 to 0.2%. where Al less than 0.01% or NO
If A1 is less than 2% or N is less than 0.0006%, a sufficient amount of A&N cannot be generated, and therefore the inhibitor cannot have the effect of suppressing the growth of primary recrystallized grains. If it exceeds 2%, the residual magnetic flux density of the finally obtained magnet alloy will decrease.

Next, the specific process of the manufacturing method will be explained.

First, a molten alloy having the above-mentioned composition is melted by vacuum melting or other appropriate means, and then cast by a known casting means such as vacuum casting to form an ingot. Then, after hot forging as necessary, (temperature at which 50% α phase exists in the (α+γ) phase +50°C} to (melting point -50°C)
Hot rolling is carried out at a temperature range of 1 to obtain the desired thickness. Here, the temperature at which 50% of the α phase exists in the ((α+γ) phase + 5
The specific temperature range from 0℃} to (melting point = 50℃} varies depending on the component composition, but typical component compositions of water systems are Cr28-32%, Co15-18%, MO2-4%,
If the balance is Fe, the temperature is 800 to 1550°C.
Pi! degree.

In this hot rolling, the average reduction rate per pass was 5
．． Within the range of 0-90%, and the total rolling reduction rate is 40.0-90%.
It is desirable that it be within the range of 99%. As already mentioned! #Finally, in order to obtain the 1101<100> texture, it is necessary to introduce a certain amount of strain in the hot rolling process, and the average rolling reduction per pass is 5.0.
% or the total rolling reduction is less than 40.0%, it becomes difficult to finally obtain a (110}<100> texture parallel to the rolling direction. Also, if the average rolling reduction per pass is 9.
In the case of applying strong processing that exceeds 0%, or in the case of applying strong processing that causes the total reduction rate to exceed 99%,
Conversely, secondary recrystallization in which the (110}<100> axis is parallel to the rolling direction may not be preferentially generated. Therefore, it is difficult to obtain a texture in which the (110}<100> axis is oriented parallel to the rolling direction. In order to obtain a magnet with sufficiently excellent magnetic properties in the direction parallel to the rolling direction, it is desirable to set the rolling reduction rate in the hot rolling process within the above range.

After hot rolling, in the method of the invention of claim 2 and the invention of claim 4, primary recrystallization annealing is performed in the α+γ) phase region, and in the method of the invention of claim 3 and the invention of claim 5, In the case of this method, primary recrystallization annealing is performed in the single phase region of α phase, and then heat treatment is performed in the (α+γ) phase region. Here α
The temperature of the primary recrystallization annealing in the single-phase region should basically be within the α single-phase temperature range, and specifically varies depending on the component composition, but in the case of the above-mentioned typical component composition, it is 1150 to 1300.
The heating time may be approximately 0.2 to 4 hours. On the other hand, the temperature in primary recrystallization annealing or heat treatment in the (α + γ) phase region ((α + γ) phase heat treatment after primary recrystallization annealing in the α phase single phase) is (
The temperature may be within the two-phase region of α+γ), and specifically varies depending on the component composition, but in the case of the above-mentioned typical component composition, the temperature may be about 800 to 1250°C. Also (α+
The heating time in the γ) phase region is approximately 0.5 to 10 hours when the primary recrystallization annealing is also performed, and when the heating time is not also the primary recrystallization annealing (i.e. heating after the primary recrystallization annealing in the α phase region) ) may be set to about 0.1 to 0.5 hours. The average grain size of the primary recrystallized grains in the α phase region or α+γ) phase region due to the primary recrystallization annealing is approximately 0.01 to 1 mm.

As mentioned above, after the primary recrystallization annealing or heat treatment in the (α + γ) phase region, in the case of the invention of claim 4 or the invention of claim 5, heat treatment in the α + γ + σ) phase region is performed. Secondary recrystallization annealing is performed, and in the case of the invention of claim 2 or claim 3, secondary recrystallization annealing is performed immediately.

Here, heating in the (α + γ + σ) phase region is essentially (α + γ
+σ) The specific target temperature varies depending on the component composition, but in the case of the above-mentioned typical component composition, it may be about 700 to 1000°C, and the heating holding time is 0. It is preferable to set it as about 2 to 5 hours. Further, the secondary recrystallization annealing may be performed in the α phase single phase region, but specifically, it may be heated at about 1150 to 1300° C. for about 0.2 to 20 hours.

As described above, by performing secondary recrystallization annealing, the average crystal grain size can be reduced to 2. Oram or higher, it is possible to obtain a magnet alloy material having a texture in which the (110}<100> axis is highly oriented in a direction parallel to the rolling direction. in the direction (
110}<100> axis-oriented texture has an accumulation degree of 5
0% or more is desirable in order to obtain excellent magnetic properties in the direction parallel to the rolling direction in the final magnet, but by manufacturing through the steps described above, the average grain size can be reduced to 2.0%. If it is Ornm or more, the integration degree is easily 5.
It is possible to secure 0% or more.

In order to actually use such magnet alloy materials as magnets, after further solution treatment and quenching,
A treatment for magnetically hardening, in other words, a heat treatment in a magnetic field (aging in a magnetic field) for spinodal decomposition and a secondary aging treatment are performed.

Here, the solution treatment can be performed by quenching at a temperature of about 1000 to 1300°C, but it may destroy the texture obtained by the secondary recrystallization described above and generate crystals with random orientation or crystals deviated from the desired direction. In order to prevent the growth of oriented crystals, it is desirable that the heat treatment temperature for solution treatment be lower than the secondary recrystallization temperature. It is also possible to perform solution treatment using the cooling process immediately after secondary recrystallization annealing, and in that case, it is not necessary to heat only for solution treatment after secondary recrystallization annealing.

The heat treatment in a magnetic field and the secondary aging treatment after the solution treatment and quenching may be performed as follows.

That is, as has been conventionally proposed for Fe-Gr-Co magnet alloys, 630 to 7
Constant temperature heat treatment (aging treatment in magnetic field) at about 0.00℃ to 0.25
It is carried out for about 4 hours, and then heated to 0 at around 600 to 500℃.
．． Aging treatment is performed for about 5 to 40 hours.

In this way, a single magnetic domain ferromagnetic phase is dispersed and precipitated in the nonmagnetic phase due to spinodal transformation, and the single domain ferromagnetic phase particles are aligned in the direction of the magnetic field. As mentioned above, after secondary recrystallization annealing, a texture is obtained in which the axis of easy magnetization (110}<100> is aligned in the direction parallel to the rolling direction. Therefore, the alloy is further If heat treatment in a magnetic field and aging treatment are performed while applying a magnetic field in a direction parallel to the rolling direction, the above-mentioned texture and magnetic field treatment effect combine to form a single magnetic domain with a significantly high orientation rate. The shaped ferromagnetic phase particles are precipitated in a direction parallel to the rolling direction, resulting in a magnetic alloy with significantly high anisotropic magnetic properties.

Example Examples and comparative examples of this invention are described below.

[Example 1] Cr30%, Co15%, MO3%, Ti0.3%, M
An alloy consisting of NO, 1%, SO, 05%, and the balance consisting of Fe and unavoidable impurities is melted and cast according to a conventional method, and the resulting ingot is heated to 1200°C and hot forged to form a thick The length was set to 20 mm, and then hot rolling was performed by heating to 1200° C. again. This hot rolling has a reduction rate of 5 to 9 per pass.
Various changes were made within the range of 0%, and the total rolling reduction was set at 90% to obtain a hot rolled sheet with a thickness of 2 mm. Note that some samples were not hot rolled, and the rolling reduction per pass was 0% and the total rolling reduction was 0%. After that, a sample in the direction perpendicular to the rolling direction and a sample in the direction perpendicular to the rolling direction (plate width direction) were cut out from each plate material, and each sample was subjected to primary recrystallization annealing in the (α+γ) phase region. After heating at ℃ for 10 minutes, water cooling and subsequent recrystallization annealing at 120
After being heated and maintained at ℃ for 15 hours, it was cooled with water. Furthermore, the following heat treatment was performed for hardening. That is, after performing solution treatment by heating at 1200°C for 1 hour and cooling with water, heating at 640°C in a magnetic field for 20 minutes, followed by aging treatment in a magnetic field by holding at 620°C for 4 hours in the same magnetic field, and then After holding at 610°C for 2 hours, it was slowly cooled to 500°C at a cooling rate of 4°C/hr.
A secondary aging treatment was carried out by holding at ℃ for 10 hours. The aging treatment in a magnetic field was performed by applying a magnetic field in a direction parallel to the rolling direction or by applying a magnetic field in a direction perpendicular to the rolling direction.

[Comparative Example 1] An alloy having the same composition as Example 1 was treated under the same conditions as Example 1 until hot rolling, and after hot rolling, primary recrystallization annealing and secondary recrystallization annealing were performed. Instead, heat treatment for hardening was immediately performed under the same conditions as in Example 1.

Each material obtained in Example 1 and Comparative Example 1 above (
hardening treated magnets), magnetic properties,
That is, the results of examining (BH)max, Br, and 11-1c are shown in FIG. 1 in correspondence with the rolling reduction per pass in hot rolling. In Fig. 1, "parallel to the rolling direction" refers to the measurement of the magnetic properties in the direction parallel to the rolling direction of a sample subjected to aging treatment in a magnetic field by applying a magnetic field in a direction parallel to the rolling direction. "Perpendicular to the rolling direction" refers to the measurement of the magnetic properties in the direction perpendicular to the rolling direction for a sample that was subjected to aging treatment in a magnetic field by applying a magnetic field in the direction perpendicular to the rolling direction.

From FIG. 1, it is clear that the samples hot rolled in Example 1 at a rolling reduction of 5% or more per pass have significantly higher magnetic properties in the direction parallel to the rolling direction.

[Example 2] An alloy having the same composition as Example 1 was treated under the same conditions as Example 1 until hot forging, then heated to 1200°C and hot rolled at a total reduction rate of 0 to 99.9 It was applied by changing it within the range of %. Thereafter, primary recrystallization annealing, secondary recrystallization annealing, and further heat treatment for hardening were performed under the same conditions as in Example 1.

[Comparative Example 2] An alloy having the same composition as Example 1 was treated in the same manner as Example 2 until hot rolling, and then immediately hardened without performing primary recrystallization annealing and secondary recrystallization annealing. The heat treatment for this purpose was performed under the same conditions as in Example 1.

The results of examining the magnetic properties of each of the materials obtained in Example 2 and Comparative Example 2 are shown in FIG. 2 in correspondence to the total reduction ratio of hot rolling.

From Figure 2, it can be seen that in Example 2, the total reduction rate of hot rolling was 4
It is clear that by setting the content to 0.0% or more, a magnet with extremely excellent magnetic properties in the direction parallel to the rolling direction can be obtained.

[Example 3] An alloy having the same composition as Example 1 was processed under the same conditions as Example 1 up to hot forging, and then hot rolled for 8
The heating was carried out at various heating temperatures from 00 to 1500°C, with a rolling reduction rate of 50% per pass and a total rolling reduction rate of 90%.

Thereafter, primary recrystallization annealing, secondary recrystallization annealing, and further heat treatment for hardening were performed under the same conditions as in Example 1.

[Comparative Example 3] An alloy having the same composition as in Example 1 was treated in the same manner as in Example 3 until hot rolling, and then immediately hardened without performing primary recrystallization annealing and secondary recrystallization annealing. The heat treatment for this purpose was performed under the same conditions as in Example 1.

The results of examining the magnetic properties of each of the materials obtained in Example 3 and Comparative Example 3 are shown in FIG. 3 in correspondence with the heating temperature during hot rolling.

In the alloy having the composition used in Example 3 and Comparative Example 3, the temperature at which 50% of the α phase exists in the ((α+γ) phase +50
℃} is about 850℃, (melting point -50℃} is about 1500℃, but from FIG. 3, in Example 3, the melting point is about 850℃~
It is clear that when hot rolled by heating to a temperature within the range of 1500'C, the magnetic properties in the direction parallel to the rolling direction are significantly superior.

[Example 4] An alloy having the same composition as in Example 1 was hot forged in the same manner as in Example 1, and then heated to 1200°C with a rolling reduction rate of 50% per pass and a total rolling reduction rate of 90%. Hot rolling was performed. Thereafter, after heating at 1250°C for 30 minutes as primary recrystallization annealing in the α phase region, water cooling, and then (α+
After heating at 1000° C. for 10 minutes as heat treatment in the γ) phase region, it was cooled with water, and then heated and held at 1200° C. for 151 minutes as secondary recrystallization annealing in the α phase region, followed by water cooling. after that,
Heat treatment for hardening was performed under the same conditions as in Example 1.

[Example 5] An alloy having the same composition as in Example 1 was subjected to hot rolling under the same conditions as in Example 4. Then (α+γ)
After heating at 1000 °C for 10 minutes as primary recrystallization annealing in the phase region, water cooling, then heating at 900 °C for 1 hour as heat treatment in the (α + γ + σ) phase region, water cooling, and rough α
After being heated and held at 1200° C. for 15 hours as secondary recrystallization annealing in the phase region, it was cooled with water.

Thereafter, heat treatment for hardening was performed under the same conditions as in Example 1.

U Example 6] An alloy having the same composition as in Example 1 was subjected to hot rolling under the same conditions as in Example 4. After that, after heating at 1250 ° C. for 30 minutes as primary recrystallization annealing in the α phase region,
1 as water cooling and then heat treatment in the (α+γ) phase region.
After heating at 000℃ for 10 minutes, cooling with water, and further heating (α+γ+σ
) After heating at 900°C for 1 hour as a heat treatment in the phase region, water cooling was performed, followed by secondary recrystallization annealing in the α phase region.
After being held at 200°C for 15 hours, it was cooled with water. Thereafter, heat treatment for hardening was performed under the same conditions as in Example 1.

The results of measuring the magnetic properties in the direction parallel to the rolling direction for each sample obtained in Examples 4 to 6 are the same as those in Examples 4 to 6 among the samples obtained in Example 3. Table 1 also shows the magnetic properties in the direction parallel to the rolling direction for those heated at 1200°C.

From Table 1, Example 3 → Example 4 → Example 5 → Example 6
It can be seen that better magnetic properties are obtained in this order.

Furthermore, samples of Examples 3 to 6 and Comparative Example 3 (However, for Example 3 and Comparative Example 3, the heating temperature of hot rolling was 1
The results of examining the average grain size after secondary recrystallization annealing (200°C) were compared to each heat treatment form.
As shown in the figure.

From FIG. 4, it can be seen that 2. It can be seen that an average crystal grain size of .omm or more can be obtained. In addition, heat treatment in the α phase region may be performed before heat treatment in the (α + γ) phase region, or (
It can be seen that by performing heat treatment in the (α+γ+σ) phase region after heat treatment in the α+γ phase region, the grain size after secondary recrystallization annealing becomes even larger.

Furthermore, based on the data of Examples 1 to 6, Figure 5 summarizes the relationship between the average grain size after secondary recrystallization annealing and the magnetic properties in the direction parallel to the rolling direction after hardening treatment. Shown below.

From FIG. 5, there is a correlation between the average grain size and magnetic properties after secondary recrystallization annealing, and the average grain size is 2.0.
It is clear that when the magnetic field is greater than or equal to m, extremely excellent magnetic properties can be obtained in the direction parallel to the rolling direction.

Further, based on the data of Examples 1 to 6, the average grain size after secondary recrystallization annealing and (11
0}<100> A summary of the relationship between the degree of accumulation of the texture in the direction parallel to the rolling direction is shown in FIG. From Figure 6, the average grain size after secondary recrystallization annealing and (110}<1
00> It can be seen that there is a correlation between the degree of accumulation of the texture in the direction parallel to the rolling direction, and by setting the average grain size to 2.0 mm or more, it is possible to achieve a significantly high degree of accumulation of 50% or more. .

Therefore, from both Fig. 5 and Fig. 6, by setting the average grain size after secondary recrystallization annealing to z, omm or more, the rolling direction of the (110} <100> texture □ direction parallel to the rolling direction It is clear that the degree of integration becomes significantly high at 50% or more, and as a result, significantly high magnetic properties can be obtained in the direction parallel to the rolling direction.

Effects of the Invention The magnetic alloy of the invention according to claim 1 is a Fe-CrCo based magnetic alloy having an average crystal grain size of 2.0. m or more and has a highly integrated texture with a (110) (100> axis oriented in a direction parallel to the rolling direction),
Therefore, it can exhibit extremely excellent magnetic properties in the direction parallel to the rolling direction.

Further, according to the manufacturing method of the invention according to claims 2 to 5, it is possible to reliably and stably manufacture a magnet alloy having excellent magnetic properties in the direction parallel to the rolling direction as described above, and also without performing cold rolling. Therefore, manufacturing costs can be reduced, and variations in characteristics due to conditions of the cold rolling process can be eliminated, making it possible to obtain a magnetic alloy of stable quality.

[Brief explanation of drawings]

Figure 1 is a graph showing the magnetic properties in each direction after hardening treatment of the magnetic alloys obtained in Example 1 and Comparative Example 1 in correspondence with the rolling reduction rate per pass of the hot rolling process. A graph showing the magnetic properties in each direction after hardening treatment of the magnetic alloys obtained in Example 2 and Comparative Example 2 in correspondence with the total rolling reduction of the hot rolling process, FIG. 3 is a graph showing the magnetic properties of Example 3 and Comparative Example Figure 4 shows the magnetic properties in each direction after hardening treatment of the magnetic alloy obtained in step 3 in correspondence with the heating temperature in the hot rolling process. Figure 4 shows the heat treatment form before secondary recrystallization annealing and the secondary A graph showing the relationship between the average grain size after recrystallization annealing, Figure 5 is a graph showing the relationship between the average grain size after secondary recrystallization annealing and the magnetic properties after hardening treatment, and Figure 6 is a graph showing the relationship between the average grain size after secondary recrystallization annealing and the magnetic properties after hardening treatment. It is a graph showing the relationship between the degree of accumulation of (iio}<1oo> texture in the direction parallel to the rolling direction after secondary recrystallization annealing and the average grain size after secondary recrystallization annealing. Applicant Yama C Co., Ltd.

Claims (5)

[Claims] (1) 10 to 40% Cr (weight%, same below) and C
Fe-
In the Cr-Co based magnetic alloy, a Fe-Cr- Co-based magnetic alloy. (2) In producing a Fe-Cr-Co magnetic alloy containing 10 to 40% Cr and 3 to 30% Co, with the balance mainly consisting of Fe, after casting the molten alloy, Hot rolling is performed at a temperature within the range of the temperature at which 50% of the phase exists + 50°C} or more and the melting point - 50°C}, followed by primary recrystallization annealing in the (α + γ) phase region, and further 2 A method for producing a Fe-Cr-Co magnet alloy, which comprises performing secondary recrystallization annealing. (3) In producing a Fe-Cr-Co magnetic alloy containing 10 to 40% Cr and 3 to 30% Co, with the balance mainly consisting of Fe, after casting the molten alloy, Hot rolling is carried out at a temperature within the range of 50% phase existence temperature + 50°C} or higher and {melting point -50°C} or lower, followed by primary recrystallization annealing in the α phase region, and then (α + γ ) A method for producing a Fe-Cr-Co based magnet alloy, which comprises performing heat treatment in the phase region and further performing secondary recrystallization annealing. (4) In producing a Fe-Cr-Co magnetic alloy containing 10 to 40% Cr and 3 to 30% Co, with the balance mainly consisting of Fe, after casting the molten alloy, After performing hot rolling at a temperature within the range of not less than the temperature at which 50% of the phase exists + 50 ° C} and not more than {melting point - 50 ° C}, followed by primary recrystallization annealing in the (α + γ) phase region, A method for producing a Fe-Cr-Co magnet alloy, which comprises performing heat treatment in the (α+γ+σ) phase region and further performing secondary recrystallization annealing. (5) In producing a Fe-Cr-Co magnetic alloy containing 10 to 40% Cr and 3 to 30% Co, with the balance mainly consisting of Fe, after casting the molten alloy, Hot rolling is carried out at a temperature within the range of 50% phase existence temperature + 50°C} or higher and {melting point -50°C} or lower, followed by primary recrystallization annealing in the α phase region, and then (α + γ Fe-
Manufacturing method of Cr-Co magnet alloy.