JPS5873744A - Fe-co-mn-c alloy - Google Patents

Abstract

PURPOSE:To obtain the titled alloy consisting of prescribed percentages of Co, Mn, C and Si and the balance Fe and capable of being provided with desired magnetic characteristics by a short-time teatment under heating without requiring the strict control of the temp. dropping program and a long-time treatment under heating. CONSTITUTION:This Fe-Co-Mn-C alloy for a magnetic material consists of, by weight, 30-55% Co, 15-27% Mn, 0.3-2.0% C, <=3.6% Si and the balance Fe. When the alloy is treated under heating at a temp. giving nonmagnetic gamma-phase in a thermal equilibrium state and quenched to room temp., the gamma-phase state is maintained without causing phase transformation. The alloy is not cracked even when cold rolled, cold swaged or cold drawn at a high rate, and it maintains the nonmagnetic state and has high workability. By simply treating the alloy under heating for a much shorter time (about 1hr) than the time of a treatment under heating for a conventional alloy, desired magnetic characteristics are obtd.

Description

DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a re-Co-Mn-C alloy for magnetic materials. ” The FeCr-Co alloy currently used in various industries is known as a permanent magnet that can be easily cold-worked, such as rolling, wire drawing, and swaging. Efforts are being made to improve the magnetic properties of Fe-Cr-Co alloys.By the way, in order to obtain properties as permanent magnets, Fe-Cr-Co alloys are heat treated to disperse the strong magnetic phase and weak magnetic phase into appropriate particles. However, the heat treatment method is a 411-den temperature cage.
is lowered at a predetermined rate (e.g., 20°C/hour) and subjected to long-term O aging treatment.
．． This method requires a heat treatment time of 10 hours or more. In addition, it was necessary to strictly control the temperature drop and shielding changes mentioned above, which have a large effect on magnetic properties. In order to solve this problem, a method has been proposed in which the temperature is lowered stepwise at intervals of 10°C to 20°C instead of continuously, but this method requires a long heat treatment. The present invention is essential for heat treatment such as in re-Cr-Co alloys. ! It is a magnetic material that has the major characteristics that the desired magnetic properties can be obtained with a short heat treatment of 1 hour, without the need for strict temperature control or long heat treatment, and furthermore, the desired location can be made non-magnetic. The present invention provides alloys for materials.

The alloy for magnetic materials of the present invention contains 30 to 55% by weight of Co.
e Mn is 15 to 2711%, C is 0.3 to 2.0 IG, 81 is less than 3.6 IG, and the remainder is Pe.
It is an alloy characterized by consisting of. Fe is 910℃
In the temperature range of ~1390C, it becomes a non-magnetic bi-centered cubic structure (hereinafter referred to as r-phase), but when rapidly cooled to room temperature, it becomes a magnetic body-centered cubic structure (hereinafter referred to as r-phase).

(referred to as α phase). When adding re K Mu and increasing the amount of Mn added, the r/(γ+α) boundary widens toward the low temperature side ($), and when a small amount of C is added, the nonmagnetic r phase at high temperature changes at room temperature. can get.

The above Fe　Mn　C alloy is cold-worked to make it strong.

When the r-phase is transformed into a magnetic phase by heat treatment at a low temperature.

With a small amount of Mn, high coercive force (hereinafter referred to as Hc) cannot be obtained, and with a large amount of 2Mn, the amount of magnetization decreases.
′ Furthermore, the addition of KCo has the effect of increasing the amount of magnetization of the magnetic phase.

Further, 8i is an element that forms a γ region at high temperatures and forms a solid solution with FeK, improving the magnetic properties of the structure of the present invention.

The above-mentioned alloy of the present invention is heat treated in a temperature range in which a nonmagnetic r-phase is obtained in a state of thermal equilibrium, and then rapidly cooled to room temperature to form an r-phase without undergoing phase transformation. It is an alloy with good workability that does not crack even when subjected to cold swage and cold stretch processing at high strength, maintains a non-magnetic state, and has good workability. A major feature of the alloy of the present invention is that after performing these cold workings, the desired magnetic properties can be obtained with a simple hot section 11 in a much shorter time than conventional alloys.

Next, the details of the present invention will be explained by referring to examples.

First, 12 compositions of Al to 12 shown in Table 11 of 9th order were selected as samples. In addition, a known We Cr - Co Ti alloy was selected as a comparison rounding A13.

Table 1 tf, Table 1 t) Alloy ingots having the chemical compositions shown in A1 to A6 were heated at 1100 tl:Oj 1 degree for 1 hour.

After solution treatment in the atmosphere, 10%N 6H
It was quenched by immersing it in an aqueous solution. Small pieces are cut out from these alloy ingots and the amount of magnetization is measured.
It was ss 9 degrees. In addition, when we investigated the crystal structure using xsgi, no 1m pattern other than a double-centered cubic structure was observed, and it was confirmed that r8 was obtained in heavy form. Although it is a metal-containing ingot with a round chemical composition that falls outside the scope of claim 4, when it was subjected to O treatment in the same way as the At~60 alloy ingot, it became
The same results as A1-6 can be obtained. However, Mu1-1
and 120 Tanigane Ingot Co., each kBstx-14,
51c Gauss, Ba! 13.9 kgau
With the chemical compositions of as, tLAllTh, and 12, it was not possible to introduce the nonmagnetic r phase at room temperature. Alloy ingot 011 in r-phase state of A1-10? After removing the I oxide film,
Cold Sekishin-1 cold rolling or cold rolling was carried out, and then heat treatment was performed in an Ar atmosphere. 1st
A13 in the table is an example of a Fe-Cr-Co alloy.

The No. 413 alloy ingot was solution treated at 1180C for 1 hour in a water atmosphere and quenched by immersion in water. After that, cold wire drawing processing was performed with a placement rate of 70%, and the wire was drawn again at 65%.
Heat treated at 0°C for 1 hour in a hydrogen atmosphere, quenched in water (conditions), then heated again at 18°C from 625°C to io5°C at an O rate for 9 times (in a hydrogen atmosphere)
Hydrogen WM for another 8 hours at 505℃! Heat treatment was performed in air (condition B). 111th! Table 2 shows the relationship between the composition of the sample shown in Table 1, various processing conditions, and magnetic properties.

Samples Al to 6 in Table 2 have compositions within the claimed range of the present invention), can be heat treated in a short time, and exhibit good magnetic properties. On the other hand, A7 to A10 have compositions outside the claimed range.]
The magnetic properties are significantly inferior to the values within the claimed range. The known Fe-Cr-Co alloy can be heat-treated for 60 minutes in the same way as the alloy of the present invention, but cannot obtain magnetic properties that are inferior to the alloy of the present invention, but obtain magnetic properties equivalent to the alloy of the present invention. In order to achieve this, a long Q' ring like the conditions and condition B described above is required.

It should be noted that the alloy of the present invention is not limited to the heat treatment conditions shown in Table 2, but the temperature can be selected from appropriate heat treatment conditions in the range of 520°C to 400°C for 1 hour to 180 minutes to 300°C. Good magnetic properties can also be obtained.

Based on the results shown in Table 2, the claimed range of the composition of the alloy of the present invention is limited as follows. When CO deviates from the 30 weight S to 55 weight range, the coercive force and residual magnetic flux density (hereinafter referred to as Br) * Br
4# and the maximum energy product (hereinafter referred to as B) hnax) deteriorated. Therefore, Co needs to be in the range of 30 to 55 weight arcs. If there is a small amount of Co, it is necessary to add a large amount of Or, and if there is a large amount of Co, it is necessary to add a small amount of Or. However, when Co is 30% by mass and Mu is added by 27% by mass, the amount of magnetization decreases and becomes unusable.

When the weight is 55, for the alloy, Mnt-15
When added below the weight attack, magnetic Kl! -No alloy was obtained9. Therefore, sMa @ range is 15% by weight ~
2F heavy attack and Shie. For the alloy of the present invention with 27% Ma added by weight, it was impossible to introduce one phase at room temperature when C was added below 0.3% by weight. 90° solid solution in the alloy or phase of the present invention up to 2.0% by weight
I was able to let it go.

The alloy of the present invention containing Mfi of 27 wt. and C of 0.3 wt. can be subjected to strong cold working. .0 weight attack,
If 8i is added in excess of 3.6 times tS, it is impossible to introduce the r phase to room temperature.

As shown in Table 2 above, alloys having compositions within the claimed scope of the present invention are complex like F@-Cr-Co alloys and do not require long heat treatment, but can be easily heat treated. It was found that the material had good magnetic properties.

Furthermore, in the alloy of the present invention, the area reduction ratio of the alloy ingot is 99
≦ 9 Alloy Hososo obtained by cold wire drawing at 475℃
Continuously from one end of a through-furnace in a hydrogen atmosphere with a soaking length of 200 mm maintained at a temperature of .

Drum KII with a diameter of 400 m is fed in at a speed of 60 cm/min and taken out continuously from the other end! For example, in the case of the composition of 9Al shown in Table 1, H
c=590 (Oe)t9r=9.3(KGa
uss ) e 8q = O198, BHmax
Good magnetic properties of = 3.3 (MGmuss・Oe') were obtained.

Furthermore, another major feature of the alloy of the present invention is that after it is heat-treated to obtain the desired magnetic properties, a desired location in the resulting alloy is heated at approximately 1000°C for about i seconds. □１□
5. or. There is -1.

This will be explained using an example. The composition of A1 in Table 1 was cold swaged and heated at 440°C for 60 minutes.
The rod-shaped alloy obtained in 1 was rotated around the central axis in the longitudinal direction at a speed of I11 rotation t, and a 5W continuous wave YA
Irradiate the G laser with a rape beam of one diameter for 10 seconds.9. When we cut out the part irradiated with this laser and measured the amount of magnetization, the value of B was about 10 Gauss, which is mostly non-magnetic O.
It was confirmed that it was in the r phase. Therefore, the alloy of the present invention can be made non-magnetic at a desired location using a laser beam, an electron beam, an infrared beam, etc., and it is possible to combine magnetic and non-magnetic regions.

The alloy of the present invention can be cold-worked to a strength of 9.

It is a magnetic material that is useful in many fields.

Procedural amendment reconnaissance) 57, 12. -6 Director General of the Patent Office, Month, Day, 1980, 1, Indication of Case 1982 Patent Application No. 1543
No. 70 No. 2. Title of the invention 1.-Go-Mn-0 alloy 3. Relationship to the amended case Applicant 5-33-1 Shiba, Minato-ku, Tokyo (423) Representative of NEC Corporation Tadahiro Sekimoto 4, Agent 5-37-8 Shiba, Minato-ku, Tokyo 108, Seisei Mita Building 5, ``Detailed Description of the Invention'' column of the specification to be amended.

6. Contents of the amendment 1) In the fifth line of page 3 of the specification, the phrase [River..., rIIi body center...] has been replaced with "...Gan..., a ferromagnetic body..." 0 ゛2) In the 11th line of the 3rd page of the specification, the phrase [...gamma phase is changed to magnetic phase...] is corrected to ``heart...''. . . . The γ phase is changed to the annihilation phase . . . ” and so on.

3) On page 3, line 14 of the specification, “・old・・magnetic phase・
``...'' means [..., Strong @Sungsou...
``...'' and correction T6゜4) Mei 11a Sai, page 12, line 9, ``Machi...''
◎Procedural Amendment C Table Correct) Director General of the Patent Office 1, Indication of Case 1982 Patent Application No. 1! ! 4
No. 370 2, title of invention ffe-Go-Mn-0
System Alloy 3, Relationship with the case of the person making the amendment Applicant: 5-33-1 Shiba, Minato-ku, Tokyo (423) NEC Corporation Representative: Tadahiro Sekimoto 4, Agent 5: "Detailed Description of the Invention" column.

6. Contents of amendment (1) “Also C
A small amount of o......Song...Song...A small amount is enough. ” to be deleted.

Claims (1)

[Claims] Co: 30-55% by weight, Mn: l5-
27 weight attack, C: 0.3-2.0 weight%, 8i: 3.6
A re-Co Mn C-based alloy for magnetic materials, which is less than 100% in weight and is characterized by ζ゛ consisting of the remainder Fe.