JPS5830367B2 - Manufacturing method of semi-hard magnetic alloy - Google Patents

Description

Detailed Description of the Invention The present invention can be used for iron core materials such as relays and switches, and can be cold worked, has a high residual magnetic flux density of 16KG or more, and has a coercive force of 300e to 120e.
Fe-C with 0e.

The present invention relates to a method for manufacturing a W semi-hard magnetic alloy.

Semi-hard magnetic alloys used for relays and switches in electronic exchanges are required to have various properties depending on their design conditions.

In particular, this semi-hard magnetic alloy has good workability, has a coercive force Hc of about 300e to 1200e, and has a residual magnetic flux density Br for downsizing relays and switches.
Also, it is extremely important that the squareness is large.

Examples of these semi-hard magnetic alloys include Fe-Co-V based alloy Bicaloy, Remenda, and Fe-Mn-Co alloy, which utilize α-γ transformation.

Furthermore, there are Fe-Co-Mo alloys, Fe-Co-Nb alloys, etc. that utilize precipitation of non-magnetic intermetallic compounds into a ferromagnetic phase.

In addition, F e -N i -A using two-phase separation
A large number of alloys have been developed, such as I-Ti alloys and Fe-Cu-Co alloys that utilize the precipitation of a ferromagnetic phase in a non-magnetic phase.

These conventional semi-hard magnetic alloys have a coercive force He of approximately 200
e to 800e, the residual magnetic flux density Br is approximately 20KG to 12KG, and the coercive force He is 600e or more,
Moreover, a semi-hard magnetic alloy having a high residual magnetic flux density Br of 18 KG or more has not been developed.

In recent years, relays and switches in electronic exchanges have become smaller.
Therefore, the development of a semi-hard magnetic alloy having a higher residual magnetic flux density Br than before is awaited.

By the way, Fe-CoW alloys have been used as permanent magnet alloys as is well known.

For example, tungsten steel, which is a quench-hardened magnet that has been used since the end of the 19th century, has a W of 6φ and a C of 0.
7φ, 0.3% Cr, and the rest Fe, 1
After holding at 2000C to 1250℃ for several minutes, air cooling,
After being held at 50°C for several minutes, it was cooled with water and had a residual magnetic flux density Br of 9.5 KG and a coercive force Hc of 500e.

In addition, the quench-hardened magnetic KS steel invented by Dr. Honda et al. in 1916 has a carbon content of 0.8φ to 1.0mm and a Cr content of 1.0mm.
It is an alloy consisting of 5% to 3%, W 5% to 9%, Co 30% to 40%, the button and the rest Fe, and after hot rolling 1
After holding at 150°C to 1200°C for several minutes, air cooling, then holding at 750°C for several minutes, air cooling, and further at 950°G to
After keeping it at 1000℃, cool it in oil and martensai)! The residual magnetic flux density Br is 7.8KG~
11.5KG, coercive force He is 2000e~2600e
It has the following characteristics.

Furthermore, a small amount of Si, Mn, Mo starting from KS steel
JO-40 cobalt steel, including JO steel, has a residual magnetic flux density Br of 8KG to 10KG, with almost the same heat treatment as KS steel.
The coercive force He has a characteristic of 1200e to 2400e.

Since the above-mentioned quench-hardening magnet alloy contains C, decarburization by heat treatment must always be taken into account.

On the other hand, as a precipitation hardening magnet alloy that does not contain C, 19
12% ~1 invented by Kester et al. in Germany in 1931
5% Co, 10%-20% W.

There is an alloy in which the remainder consists of Fe.

This Fe-C. -W alloy is heated to 1200°C after hot rolling
Quenching from 1300°C, then 6008°C to 700°C
By tempering with
．． At 3KG to 12KG, the coercive force He is ]0OOe to 3
It has characteristics of 500e.

These conventionally invented Fe-Co-W alloys have been developed as permanent magnet alloys that undergo magnetic hardening only by quenching at high temperatures or tempering after quenching, and have a high residual magnetic flux density Br and square shape. Its properties were extremely low, making it unsuitable as an iron core material for relays and switches.

In order to eliminate the drawbacks of the above-mentioned conventional examples, the present invention has developed an alloy consisting of Co in a weight ratio of 5 to 40, W in an amount of 8 to 18, and the remainder Fe at a temperature of 1100°C or higher. After being held at a high temperature, quenching in water, cold working, and tempering results in a high residual magnetic flux density of 16KG or more, Br, and 300KG, which enables the miniaturization of relays and switches.
e] A method for manufacturing a semi-hard magnetic alloy having a coercive force He of 200e is provided.

The present invention will be explained in detail below.

According to the present invention, a Fe-Co-W semi-hard magnetic alloy having a high residual magnetic flux density Br that could not be obtained with conventional inventions is manufactured as follows.

1. The alloy is melted in air, vacuum or an inert gas atmosphere, and then the ingot is melted in the i! After t or hot working, the material is maintained at a temperature of 1100° C. or higher, and then quenched in water.

Next, cold working is performed at a processing rate of 60°C or more, and then tempered at a temperature range of 500°C to 900°C, so that the residual magnetic flux density Br is 16KG or more and the coercive force Hc is 300e to 1200e. characteristics can be obtained.

Cold working the alloy after quenching introduces structural anisotropy within the alloy, increases internal stress, and contributes to the refinement of intermetallic compound precipitation caused by subsequent tempering. It has a significant positive influence on the magnetic properties.

As will be described later in Example 1, in cold working after quenching, the higher the working rate, the higher the residual magnetic flux density Br, squareness, and coercive force He after tempering, and in cold working at a working rate of 60% or more, The effects of improving the residual magnetic flux density Br, squareness, and coercive force He become remarkable.

As will be described later in Example 1, the tempering temperature after cold working is suitably in the range of 500°C to 900°C.

That is, when the tempering temperature is 500°C or less, the residual magnetic flux density B
If the coercive force He is low and the tempering temperature is 900° C. or higher, the coercive force He decreases significantly and the desired magnetic properties cannot be obtained.

Table 1 shows typical examples of magnetic properties obtained with various compositions.

As can be seen from Table 1, according to the present invention, Co is 20
% ~ 32%, W is 10% ~ 15%, and the rest is an alloy consisting of Fe (sample numbers 7, 8, 9゜11.12, 13) K
$- exhibits magnetic properties with a residual magnetic flux density Br of 18 KG or more and a coercive force Hc of 600 e or more.

Moreover, according to the present invention, by changing the composition within the range of the amount of CaO from 5φ to 40φ and the amount of W from 8φ to 18φ,
The residual magnetic flux density Br is 16KG or more, and the coercive force Hc is 30
A wide range of magnetic properties from 0e to 1200e can be obtained.

The component ranges of these semi-hard magnetic alloys according to the present invention are as described above, and the amounts of each component element can be defined by the following reasons.

1ZW is the squareness (Br/B2) as shown in Table 1.
5o) and is extremely effective for increasing the coercive force He.

However, if the amount of W is less than 8φ, 300e
If the above coercive force Hc cannot be expected and the amount of W is more than 18, the residual magnetic flux density Br of 16 KG or more, which is the main objective of the present invention, cannot be obtained and the coercive force Hc becomes too high. It enters the realm of permanent magnets, further deteriorating cold workability.

Next, as shown in Table 1, Co has a residual magnetic flux density Br
, squareness (Br/B230), and retention force Hc.

However, when the amount of Co is less than 5, the squareness (Br/B230) h and coercive force He decrease,
Moreover, the residual magnetic flux density Br of 16 KG or more, which is the main objective of the present invention, cannot be obtained.

Moreover, if the amount of Co is more than 40, the cold workability required for the present invention is significantly deteriorated.

Embodiments of the present invention will be described below with reference to the drawings.

Example I An alloy composition consisting of 20% Co, 15% W, and the rest Fe was heated in an argon gas atmosphere, and a round ingot obtained by dissolving 0.5% Mn as a deoxidizing agent was prepared. 1300
It was quenched in water from 1300°C, cold swaged to a predetermined diameter of 1, and then quenched again in water at 1300°C.

This quenched sample was not subjected to cold swaging, and
The magnetization curve when tempered at 10° C. for 1 hour is shown by 1 in FIG.

The magnetization curves obtained when the shredded and quenched sample was subjected to cold swaging processing with a processing rate of 82% and 96 stripes, and then tempered at 710° C. for 1 hour are shown at 2 and 3 in FIG.

As shown in Figure 1, after quenching from 1300℃,
In a sample tempered at 710°C without cold swaging, the residual magnetic flux density Br is 10.0 KG and the coercive force Hc is 650e.

In addition, in a sample that was hardened from 1300°C, cold swaged at a processing rate of 82, and tempered at 710°C, the residual magnetic flux density Br was 17.2KG, and the coercive force He
was 820e, and in a sample subjected to cold swaging processing at a processing rate of 96°C and tempered at 710°C, the residual magnetic flux density Br was 18.4 KG and the coercive force Hc was ]050e.

As described above, the residual magnetic flux density Br of the sample quenched from 1300° C. and then tempered without cold swaging is extremely low.

On the other hand, the residual magnetic flux density Br, b and coercive force Hc of the sample quenched from 1300°C, cold swaged and tempered are very high, and as the processing rate increases, the residual magnetic flux density Br after tempering increases. The coercive force He increases and clicks,
Cold swaging before tempering is very important to obtain the desired magnetic properties.

In addition, Table 2 shows that after cold aging processing with a processing rate of 96 strips,
This shows the magnetic properties when tempered at each temperature for 1 hour.As shown in Table 2, by changing the tempering temperature, the residual magnetic flux density Br is 16KG or more, and the coercive force He
Magnetic properties of 360e to 1050e can be obtained.

Example 2 20% Co is kept constant, W is 5% and 10%.

A round ingot obtained by dissolving each alloy composition of 13φ with the remainder consisting of Fe in an argon atmosphere and dissolving 0.5 tons of Mn as a deoxidizing agent was quenched in water at 1300'C. FIG. 2 shows the magnetization curve when the material was subjected to cold swaging processing at a processing rate of 96% and tempered at 720° C. for 1 hour.

In FIG. 2, 1 is the magnetization curve of an alloy containing 5 W, 2 is 10 W, and 3 is 13 W.

As can be seen from Figure 2, in an alloy consisting of 20% Co, 5% W, and the rest Fe, the residual magnetic flux density Br is 16.
7KG, squareness Br/B25O is 0.70, coercive force He is] 90e, 20% Co, 10% W,
In an alloy where the remainder is Fe, the residual magnetic flux density Br is 18
．． 2KG, the squareness Br/B2g□ is 0.85, the coercive force He is 480e, 20 pieces of Co, 13 pieces of W,
In an alloy where the remainder is Fe, the residual magnetic flux density Br is 19
．． At 0 kg, the squareness Br/B28o is 0.92 and the coercive force He is 770e.

In this way, as the amount of W increases, the squareness Br/B2
80 and coercive force Hc increase.

For reference, FIG. 2 shows an example of a conventional semi-hard magnetic alloy having a high residual magnetic flux density Br.

4 in Fig. 2 is Remendar alloy (■ is 3.5φ, Mn is 0,
5% is the magnetization curve of 48% tCo and the rest is Fe), and 5 is the magnetization curve of Fe-Mo-Co alloy (Mo is 13%).
This is a magnetization curve with 20 φ and co, and the rest Fe.

As can be seen from FIG. 2, Fe-Co-W according to the present invention
The alloy has a significantly higher residual magnetic flux density Br compared to conventional semi-hard magnetic alloys.

As explained above, the present invention provides a method for manufacturing a cold-workable Fe-Co-W semi-hard magnetic alloy having a residual magnetic flux density Br of 16 KG or more and a coercive force He of 300e to 1200e. It has a great practical effect as a core material for relays and switches in electronic exchanges.

[Brief explanation of the drawing]

FIG. 1 shows the magnetization curve of an alloy consisting of 20% Co, 15φ W, and the rest Fe, and FIG. 2 shows the magnetization curve of the Fe-co-W semi-hard magnetic alloy according to the present invention and the conventional FIG. 3 is a diagram showing the magnetization curve of a semi-hard magnetic alloy.

Claims (1)

[Claims] 1 A ternary alloy with a weight ratio of 5 to 40 pieces of CaO, 8 to 18 pieces of W, and the rest of Fe is 1100 pieces.
After hardening at a temperature of 16°C or higher, cold working is performed at a processing rate of 60° or higher, and tempering is performed at a temperature range of 500°C to 900°C.The residual magnetic flux density is 16KG.
The above is a method for manufacturing a semi-hard magnetic alloy having a coercive force of 300e to 1200e.