JPS5873748A - Fe-co-mn-c alloy - Google Patents

Abstract

PURPOSE:To obtain an Fe-Co-Mn-C alloy having favorable magnetic characteristics by a simple treatment under heating by preparing an alloy with specified percentages of Co, Mn, C, V and Fe. CONSTITUTION:An alloy consisting of, by weight, 30-55% Co, 15-27% Mn, 0.3-2.0% C, <=2.9% V and the balance Fe is prepared. 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 cold worked and simply treated under heating for a short time such as about 1hr to obtain desired magnetic characteristics. By heating the desired part of the alloy at about 1,000 deg.C for about 1sec and quenching it after obtaining the desired magnetic characteristics, the part can be made nonmagnetic.

Description

DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a Fe-Co-Mn-C alloy for magnetic materials.

Fe-2-Or--Co alloys, which are currently used in various fields, are known as permanent magnets that are easy to cold-work, such as rolling, rolling, and swaging. Efforts are therefore being made to further improve the magnetic properties. By the way, Fe = Cr
For the -Co- alloy, a heat treatment method is used in which the "strongly magnetic" phase and the "St%/% magnetic" phase are divided into appropriate fractions in order to obtain properties as a permanent magnet. however,
The heat treatment method is to heat a specific temperature range slowly at a predetermined rate of 11! This is a method in which the material is cooled at a temperature of 20 DEG C./hour, for example, and then subjected to a long aging treatment, which requires a heat treatment time of 10 hours or more. Furthermore, it was necessary to strictly control the rounding and temperature drop curves, in which the degree of convergence greatly affects the magnetic properties. In order to solve this problem, instead of continuously decreasing the temperature, we
A method has been proposed in which the temperature is lowered stepwise at intervals of 20°C, but this requires a long heat treatment for the inside.

The present invention is based on *thermal J6! such as in Fe-Cr-Co alloys. The desired magnetic properties can be obtained with a short heat treatment of 1 hour, and the desired location can be made non-IAAA, without the need for strict temperature-lowering program management or long-term heat treatment required for IK. An alloy for magnetic materials that has the following characteristics is commonly used.

The o11&gold material of the present invention contains 30 to 55% by weight of Co, 5 tons of Mn #15 to 27, and 0.3 to 2.0 c.
Weight L V is 2.9 weight curse or less and the rest is F1! It is an alloy characterized by consisting of. Fe is 910℃~
Non-magnetic face-centered cubic structure (hereinafter referred to as
(referred to as γ phase), but when rapidly cooled to room temperature.

It has a magnetic body-centered cubic structure (hereinafter referred to as α phase).

When FeK- is added and the amount of Mn added is increased, 17(r
+α) The boundary moves toward the low temperature side, and.

When a small amount of C is added, a high-temperature, non-magnetic γ phase is obtained at room temperature.The above-mentioned FeMnC alloy is strongly cold worked and heat treated at a low temperature to transform the γ phase into a magnetic phase. When a small amount of aluminum is used, it has a high coercive force (or less).

If a large amount of e Mn is not obtained (referred to as Hc), the amount of magnetization decreases. Furthermore, the addition of KCo has the effect of increasing the amount of magnetization of the magnetic phase.

Further, V is an element that forms an r region at high − re K, forms a solid solution, and improves the magnetic properties of the alloy of the present invention.
:, :,.

The above-mentioned alloy of the present invention is heat-treated in a temperature range in which a non-magnetic r-phase is obtained in a -equilibrium state, and then rapidly cooled to room temperature to form an r-phase state without phase transformation. l.

It was found that the alloy does not crack even when subjected to severe cold arc, cold swage and cold wire drawing, maintains a non-magnetic state, and has good workability.9. A major feature of the alloy of the present invention is that after performing these O cold workings, the desired magnetic properties can be obtained by simple heating in a much shorter time than with conventional alloys.

Next, the details of the present invention will be explained with reference to examples.

First, 12 types of compositions A1-12 shown in Table 1 were selected as samples. A known re-Cr-Co-Ti alloy was selected as the ninth A13 of the nine comparisons.

The alloy ingots having the chemical compositions shown in Al to 6 in Table 1, tfsst', were solution-treated at a temperature of 1100 t for 1 hour in an Ar atmosphere, and then quenched by immersing them in a 10-stroke NaOH aqueous solution. Each small piece from these alloy ingots@
l) and measure the amount of magnetization.

The saturation magnetic flux density (hereinafter referred to as Bs) is 10Ga in both cases.
uss 11 degrees and i5. In addition, when the crystal structure was examined by XSA folding, no fDB folding pattern other than a bicentered cubic structure was observed, confirming that rll14 was obtained at room temperature. A7 to 12 are alloy ingots with round chemical compositions that are outside the scope of the present invention.
When subjected to the same treatment as the l~60 alloy ingot,
The same results as Al-6 were obtained for samples 7-1o. However, All and Al2O alloy ingots each have a
! 14.5 KGasiss eBs = 13.8
K Gauss 31. With the chemical compositions of All and A12, the nonmagnetic or phase cannot be brought to room temperature. A
After removing the 0 surface oxide film, the alloy ingot in the 1 to 100r phase state is subjected to cold wire drawing, cold swaging, or cold straight arc processing, and is then processed to a wire width of 70 mm.

Heat treatment was performed in an Ar atmosphere. 413 in m1 table is Fe
-Or - This is an example of a Co-based alloy. The A130 alloy ingot was solution-treated at 1180°C for 1 hour in a water atmosphere, then quenched by immersion in water.

After that, it was subjected to cold stretching S processing with a 70% inertness rate, and again.

Heat treatment was performed at 650°C for 1 hour in a hydrogen atmosphere.

Nine (conditionum) quenched in water. After that, the temperature of the hot part Im is reduced again from 625°C to 505°C at a rate of 18°C/hour.
(Hydrogen x m atmosphere) and further heat treatment was performed at 505° C. for 8 hours in a hydrogen atmosphere (condition B).

11th! Table 2 shows the relationship between the composition of the sample shown in , various processing conditions, and magnetic properties.

S++.

j112 table Note) Conditions M and B in Tables 1 and 9 are the conditions described above.

Samples ^1 to 6 in Table 2 have compositions within the claimed range of this summary, can be heat treated in a short time, and exhibit good magnetic properties. On the other hand, the compositions of companies A7 to 10 were outside the claimed range, and the magnetic properties were significantly inferior to those within the claimed range.

In addition, the known Fe-Cr-Co alloy can only be obtained with considerably inferior magnetic properties when subjected to the same 60-minute heat treatment as the alloy of the present invention, and in order to obtain magnetic properties equivalent to the alloy of the present invention, it is necessary to Condition Person and Condition B require long-time processing.

Note that the alloy of the present invention is not limited to the heat treatment conditions shown in Table 2, and the temperature is 520°C to 400°C for 9 hours a.
By selecting appropriate heat treatment conditions in the range of 180 minutes to 3 minutes, particularly good magnetic properties can 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 falls outside the range of 30 to 55 weight, the coercive force and residual magnetic flux density (hereinafter referred to as "") e Br
4 e and the maximum energy product (hereinafter referred to as BHmax) were degraded. Therefore, Co needs to be in the range of 30 to 55 weight arc. Also, if Co is small, it is necessary to add a lot of Cr, but if Co is large, Cr should be added.
A small amount is sufficient. However, when Co is 30% by weight, i is 27
If a large amount is added, the amount of magnetization will decrease, making it more practical.

When J- is 55% by weight, magnetically hard alloys can be obtained by adding J- to the alloy below 15% by weight.
= Rita. Shi9 is 6 and J-'s range is 15 weights to 27 weights. For the alloy of the present invention, when 27 wt.
It is impossible to introduce the phase to room temperature. 90 is 2
．． The alloy of the present invention in which 27% by weight of 0M11 and 0.3% by weight of C, which were able to be solid-dissolved in the R phase of the alloy of the present invention at 0% by weight, could not be subjected to high-strength cold working. was completed. Shi9 is 9, C range is 0.3 weight attack ~ 2.0 weight ≦
And so. When (2) is added in excess of 2.9% by weight, it is possible to introduce the r phase to room temperature.

As shown in Table 2 above, the alloys having the composition within the scope of the claims of the present invention are complex alloys such as *Fe-Cr-Co alloys, and do not require long heat treatment, but can be easily heat treated. It was found that it has good magnetic properties.

Furthermore, the alloy ingot of the present invention has an area reduction ratio of 99
The alloy thin wire obtained by cold wire drawing at 480℃
Continuously from one end of a through-furnace in a hydrogen atmosphere with a soaking length of 200 mm maintained at a temperature of .

For example, the composition of the mulch shown in Table 1 can be obtained by a heat treatment method in which the weaving is carried out at a speed of 60 cm/min, the other end is continuously woven, and the mulch is deposited on 400 drums in diameter. Then Hc
= 570 (Oe), Br = 9.4 (K
Gaus@).

8q = 0.97* BHmax = 3.2 (M
Gausa・Oe)'s excellent magnetic properties were obtained.

Another major feature of the alloy of the present invention is that after it has been heat-treated to obtain the desired magnetic properties, it can be heated at a desired location in the alloy at approximately 1000°C for 1 second at S degrees, and then rapidly cooled. ,
Part 1. -:,'- is to become non-magnetic. I will clarify. The rod-shaped alloy obtained by cold swage processing and heat treatment at 440°C for 60 minutes for the composition 'A1 in Table 1 was rotated at a speed of 1 revolution/second about the central axis in the longitudinal direction, and 5W A radar beam of 1 m diameter from a continuous wave YAG laser was irradiated for 10 seconds. When we cut out the part irradiated with this laser and measure the amount of magnetization, B
It was confirmed that the 10 value was about 1O Gauss, and that it was mostly in the nonmagnetic 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.

As mentioned above, the alloy of the present invention can be easily cold-worked to a strength of 1.

Thermogeography also has the characteristic of being non-magnetic, and it also has the characteristic of being able to make a desired part non-magnetic.
It is a useful magnetic material in many fields.

゛ Procedural amendment (Usu'L) Showa ♂ 6° 1 15th Japan Patent Office Commissioner 1, Indication of case 1981, Patent Application No. 154
No. 373 No. 2, Title of the invention Fe-OFe-0o-based alloy 3, Relationship with the person making the amendment case Applicant: Tokyo Kogyo;
5-33-1 Shiba, Miyakominato-ku (423) NEC Corporation Representative Tadahiro Sekimoto 4, Agent 5, ``Detailed Description of the Invention'' column of the specification to be amended.

6. Contents of the amendment (1) In the specification, page 1 O, lines 1 to 3, ``Also, there is a small amount of CO...++＊+＊+,...
・・・・・・・・・A small amount is ↓. ” to be deleted.

Procedural amendment letter 57.12. -6 Director General of the Japan Patent Office, Month, Day, 1980, 1, Indication of Case 1982 Patent Application No. 15437
3 No. 2, Title of the invention. -0°-1. -01 go.

3. Relationship between the person making the amendment and the case Applicant: 5-33-1-4 Shiba, Minato-ku, Tokyo; Agent: 5-37-8, Shiba, Minato-ku, Tokyo 108; Resident: Mita Building 5; Amendment: ``Detailed description of the invention'' in the subject specification.

6. Amendments to the same υ・Page 3, line 5 of the specification [The essence of magnetism...o
j is corrected to ``The true meaning of ferromagnetism...''.

2)・Page 3, line 10 of the specification “・・・・・・,・
・・・・・・Convert the γ phase to a low sex phase'' is replaced with ``...
,......The γ phase is changed to a ferromagnetic phase.''

3) The 13th bamboo of the 3rd chapter of the Jin Dynasty [......]. ---
1. The text "low phase injection magnetization it" should be replaced with "......
..., the magnetic phase of the ferromagnetic phase is corrected as ".

4) Correct the phrase ``...magnetism'' in the 12th order, 8th column of the specification to read ``...-1 ferromagnetism.'' .

Claims (1)

[Claims] For magnetic materials characterized by Co: 30 to 55 weight s, Mn: 15 to 27 weight s, C: 0.3 to 2.0 weight %, V: 2.9 weight % or less, and the lower balance consists of Fe. Fe-Co-MnC alloy.