JPS60138013A - Production of magnetic alloy having rectangular hysteresis and production of reed piece and reed switch - Google Patents

Abstract

PURPOSE:To produce a magnetic alloy and reed piece which have large residual magnetic flux density, have an excellent square expanding rate and rectangular hysteresis characteristic and permit easy forging and working by subjecting a specifically composed magnetic alloy to a soln. heat treatment, heating treatment and cold working treatment. CONSTITUTION:The alloy of the compsn. contg. 0.5-20% one or >=2 kinds in total among Nb, Ta, Mo and W and 0.01-6% one or >=2 kinds in total among V, Cr, Ni, Cu, Co, Ti, Zr, Hf, Si, Al, Ge, Ga, Sn, Sb, Be, Mn, Au, Ag, platinum group element, rare earth element and C and consisting of the balance Fe is melted. The casting ingot of such alloy is subjected to a soln. heat treatment, heating treatment at 400-900 deg.C, cold working at >=50% reduction ratio and heating treatment at 500-1,000 deg.C, by which the production of the magnetic alloy having rectangular hysteresis and reed piece having an excellent magnetic characteristic and easy workability is made possible.

Description

DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a method for manufacturing a magnetic alloy and a method for manufacturing a reed piece used in beam manent reed switches, memory elements, ferrets, latching relays, etc., and the reed switch. An object of the present invention is to obtain a rectangular hysteresis magnetic alloy, a reed piece, and a reed switch, which have a rectangular hysteresis characteristic with a large residual magnetic flux density and an excellent angularity, and are easy to forge and process.

Currently, it is used as a magnetic material for reed switches, memory elements, ferreeds, and latching relays in electromagnetic equipment.
It has a large residual magnetic flux density and exhibits squareness hysteresis.
A prismatic magnetic alloy having a coercive force of several Oersteds to several 100 Oersteds is used depending on the application. Some of these products require advanced processing or work such as glass sealing, so it is desirable that they have excellent processability and that their magnetic properties remain stable even when heated at high temperatures. It is rare.

Conventionally, alloys are inexpensive and have excellent workability as magnetic materials having such characteristics, but they have the disadvantage that their magnetic properties deteriorate significantly when heated at high temperatures, and Fe-Co alloys and Fe-Ni alloys The alloy contains a large amount of expensive cobalt or nickel, and requires advanced processing techniques, so it is difficult to say that it is industrially satisfactory.

Previously, the present inventors developed a Fe-Nb alloy (Japanese Patent Publication No. 51-8
No. 1088, Special Publication No. 56-2140), Fe-'ra
alloy (Special Publication No. 5 a-La 1a No. 49), Fe-
MO-based alloy (JP-A-58-108824) and Fe
- W-based alloys (Japanese Patent Application Laid-Open No. 108823/1982) proposed that they are angular hysteresis magnetic alloys with a coercive force of 2 or more, but the present invention improves the angularity of these alloy systems. This invention relates to a method for manufacturing a rectangular hysteresis magnetic alloy with excellent angularity, a method for manufacturing a reed piece, and a reed switch thereof.

Reed switches must operate stably and accurately using pulsed magnetic fields, and for this purpose, the magnetic alloy used for the reed pieces must have a coercive force of several Oersteds to several tens of Oersteds, and have a rectangular shape ((BH) m: maximum If the energy product (energy product) is good, the power can be maintained.

In the conventional manufacturing method of the above-mentioned prior application, as shown in Figure 2, square magnetic properties were imparted by applying cold working after solution treatment and then heat treatment. As the precipitation progresses, the precipitates are non-uniform and non-uniform, so a hysteresis loop (
Even if the squareness ratio is good as shown by the dotted line), the alloy has a poor squareness ratio in the second quadrant.

The present inventors have conducted numerous studies on manufacturing methods for magnetic alloys with excellent angularity, and have found that the precipitation phenomenon progresses by atomic diffusion.
Since the precipitation process is carried out in two stages: generation of precipitation nuclei and growth of the precipitation nuclei, the heat treatment performed after solution treatment is two-stage. A method was adopted in which a large number of precipitated nuclei were generated as possible, and then a second stage heat treatment (tempering) was performed to grow these precipitated nuclei to an appropriate size.

That is, to explain the manufacturing method of the rectangular hysteresis magnetic alloy and the manufacturing method of the lead piece of the present invention with reference to the drawings, L (see Figure 8C): Solution treatment → second stage heat treatment → cold working → lead piece Piece forming> → 1st stage heat treatment λ (see Figure 8 C) Solution treatment → cold working → <Lead piece forming> → 2nd stage heat treatment → Lead piece forming> → 2nd stage heat treatment (However, (Refer to Figure 8 C) Solution heat treatment → cold working → 1st stage heat treatment → cold working → lead piece forming> → 2nd stage Heat Treatment The solution treatment described above is carried out by appropriately selecting the heating humidity and heating time depending on the composition of the alloy. , air cooling, etc.) to form a supersaturated structure and freeze the lattice defects, and in the heating applied after cold working,
This is necessary to increase the coercive force by precipitating fine intermetallic compounds.

In addition, the above cold working is performed by swaging, wire drawing, rolling, pressing, etc., and has the effect of increasing magnetic anisotropy by orienting the easy magnetization direction of the crystals of the alloy structure in the processing direction, and also has the effect of increasing magnetic anisotropy. It has the effect of uniformly dispersing the precipitated nuclei of the compound and at the same time increasing the orientation, and also has the effect of introducing lattice holes and promoting the formation of a large number of precipitated nuclei during the next heat treatment. These effects are remarkable when the above processing is applied.

In addition, the purpose of the first stage heat treatment described above is to promote the formation of a large number of minute precipitation nuclei, which are the initial stages of precipitation, using lattice defects and grain boundaries introduced by solution treatment and cold working as sources of generation. In addition, the second stage heat treatment aims to remove processing strain, recrystallize, and moderately grow uniformly dispersed fine precipitate nuclei to obtain a desired coercive force. Therefore, the temperature of the first stage heat treatment is generally relatively lower than or substantially different from the temperature of the second stage heat treatment, and is also fundamentally different from conventional heat treatments. These heat treatments are carried out in the air, preferably in a non-oxidizing atmosphere or in vacuum, with the heating temperature and heating time appropriately selected depending on the alloy composition. Great effect. That is, at temperatures below 400°C, the movement of atoms is small and precipitation becomes difficult, and at temperatures above 100''C, squareness is impaired due to disappearance of magnetic anisotropy and phase transformation, resulting in a decrease in coercive force.

According to the manufacturing method of the present invention, the base of the alloy structure has an orientation of easy magnetization in the direction of cold working, and furthermore, fine intermetallic compounds of uniform size are uniformly dispersed and precipitated in this base, so that
In a reverse magnetic field with the magnitude of coercive force (Hc), the pinned domain wall completes its movement in one fight, so the first
A magnetic alloy and a lead piece exhibiting a square hysteresis loop with excellent angularity as shown in Figure b (solid line) can be obtained.

Conventionally, lead pieces are manufactured by applying heat treatment to obtain rectangular magnetic properties, and then forming a lead piece in the shape shown in Figure 4 by machining, cutting, etc. at the point marked X in Figure 2. However, with this method, scratches and cracks are likely to occur during lead piece forming due to precipitation hardening and weakening of the alloy structure due to the growth of precipitates, and the magnetic properties are significantly deteriorated due to processing strain. Since it cannot be used as a lead piece in this state, recovery heat treatment (dotted line) is applied to remove processing strain, but it has many drawbacks such as not recovering its original magnetic properties.

As a result of various studies, the inventors found that FIGS. 2 and 3 A and B
, we have found a method for manufacturing lead pieces that does not have these drawbacks by molding the lead pieces at the point marked with * before growing the precipitates in the manufacturing method for O.

That is, according to the method for producing a lead piece of the present invention, the lead piece is formed in a state where there is no growth of precipitates, so there are no scratches or
There is no occurrence of cracks, and the heat treatment after forming the lead pieces can simultaneously remove processing strain and achieve appropriate growth of precipitates, so there is no need for recovery heat treatment as in conventional methods, and the accompanying deterioration of magnetic properties. Nor.

Next, the method for manufacturing the alloy of the present invention and the method for manufacturing the lead piece will be specifically described with reference to Examples.

Example 1 Alloy number 86 (composition Fe-75%, Nb-2%, MO-
8%.

Co-20%) alloy and lead piece manufacturing 99.9%
Purity electrolytic iron, 99.8% purity niobium, molybdenum and cobalt were used. 800 raw materials to make a sample
After melting Q in a high-frequency induction electric furnace in a vacuum, 0.5% Mn was added as a deoxidizing agent, and the mixture was thoroughly stirred to obtain a homogeneous molten alloy. Next, pour it into the mold, and the obtained ingot is about 12
It was forged at 00℃ and made into a round bar with a diameter of 10 degrees. This is 11
Intermediate annealing at 00°C and cold drawing were repeated to obtain a wire with a diameter of about 2.0 degrees. This wire was heated in a vacuum at 1000°C for 1 hour, cooled with water, and subjected to solution treatment, then heated at 600°C for 80 minutes as a first stage heat treatment, and then cold drawn to a diameter of 0.55 mm. I made it into a thin line. The processing rate (area reduction rate) in this case is 92%. Furthermore, the length is 25 from this line
A sample of 7 cm was cut out and subjected to the second heat treatment.
After heating at 0°C for 2 hours.

The squareness expressed as a ratio to the magnetic flux density B1oo when the residual magnetic flux density % BrN magnetic field is 100 Oe (maximum energy product) and the coercive force Ha were measured, and the following characteristics were obtained.

He-26,00e Br-19100GBr/B1o
. -0,95-(BH), /Br-Ha -0,960
In addition, after straightening and straightening the bend of the 0.551 m diameter wire in the cold drawn state described above, forming a lead piece with the dimensions shown in Fig. 4 by processing and cutting it, the second stage was prepared in the same manner. The magnetic properties of the lead piece heated at 700°C for 2 hours as heat treatment are He-26,20e Br--19100GBr/B1
oo-0,955fl) m/Br-nc-ao, 9ea
Met.

Example 2 The electrolytic iron used was tantalum and copper with a purity of 1.99.8%. The sample was melted in the air in the same manner as in Example 1, and similarly subjected to forging, intermediate annealing, and cold drawing to form a wire with a diameter of 1.8 mm. This was heated in a vacuum at 1100°C for 1 hour, air cooled, and then cold drawn to a diameter of 5 bmm (
A thin wire with a processing rate of 90%) was obtained.

Furthermore, as a first stage heat treatment, it was heated at 550''C for 80 minutes and then air cooled, and as a second stage heat treatment, it was heated at 650°C for 1 hour, and the following magnetic properties were obtained.

He -21,50e Br-16800GBr/B1
oo-0,958V(BH)m/Br-Hojo, 95
0 After straightening and straightening the thin wire with a diameter of 0.55111111 in the cold-worked state described above, it was similarly formed into a lead piece, and then heated at 550'C for 80 degrees as the first stage heat treatment.
The magnetic properties of the lead piece, which was heated for 1 minute and then further heated at 650° C. for 1 hour as a second stage heat treatment, were as follows.

Hc -21,80e Br-16850GBr/B□
. . -0,960Mef Br-He -&0.955 Also, the thin wire with a diameter of 0m55mm in the cold-worked state was heated at 550°C for 80 minutes as a first stage heat treatment, and then straightened to prevent bending. It was straightened and then formed into a reed piece. This is further heated at 650°C as a second stage heat treatment.
The magnetic properties of the reed piece heated for 1 hour were as follows.

Ha -21,40e Br -16aaOGBr/B
1oo-0,958(B)I), /Br-He-0,9
58, Example 8 00-14%) The electrolytic iron used was 7-eromolybdenum containing 65% molybdenum and 99.8% pure tungsten. The sample was melted in vacuum in the same manner as in Example 1, and similarly subjected to forging, intermediate annealing and cold MSU1 to form a wire with a diameter of 3 am.

This was heated in a vacuum at 1050°C for 1 hour, cooled in oil, and then cold drawn into a wire with a diameter of 1.2M (processing rate 84
%), which was then heated at 700°C for 2 hours as the first heat treatment.
Heated for 0 minutes.

The wire was further cold-drawn to have a diameter of 0.55111fi (processing rate 79%), and heated at 800° C. for 80 minutes as a second stage heat treatment to obtain the following magnetic properties.

He -28,,60eBr-18700GBr/B1
o. -0,967(,BH) i'Br-H total 0-963
Furthermore, the magnetic properties of the reed piece obtained by straightening the cold-worked diameter 9.55+xmO wire by straightening processing, forming it into a reed piece, and then heating it at 800°C for 80 minutes as a second stage heat treatment are KO-28. ,50e Br-18650Br, +'13
,. o-0,9654π), (Br-Ha -0,96
It was 5.

Example 4 The electrolytic iron and the 7-erotungsten containing 75% cobalt and tungsten were used. The sample was melted in an argon atmosphere in the same manner as in Example 1, and similarly subjected to forging, intermediate annealing, and cold drawing to form a wire with a diameter of 2 mm. This is 115
After heating in a vacuum at 0°C for 80 minutes, it was cooled with water, and then cold-drawn to produce a fine wire with a diameter of 0.55T1m (processing rate 92%).
). This cold-worked wire was straightened and straightened, and the reed piece was formed and heated at 700°C for 2 hours.The magnetic properties of the reed piece were HC-35,70e Br-18820GBr/Bxo.
o-0,945(nu), /nr-nc'-0,980
Met.

Table 1 shows various alloys with 1 at 1100°C.
After heating for a period of time, water cooling and solution treatment are performed, and then cold working, first stage heat treatment and second stage heat treatment are performed as described in the table based on the manufacturing method of the present invention. It showed magnetic properties.

As shown in each of the above Examples and Chapter 8), NbTa
, one or more of MO and W, total 0.
Alloy consisting of 5-20% v, ar, Ni, c
u.

co z Ti, zr, Hr, si,
Al, ae, Ga, In.

Tj! , Sn, 81), Be, In
, Au, Ag, platinum group elements, rare earth elements and 0
The alloy and lead piece produced by the manufacturing method of the present invention, which is composed of one or more of the above in a total of 0.01 to 60% and the balance Fe, has a coercive force of 2 F or more, a large residual magnetic flux density, and an excellent angularity. It has a rectangular hysteresis characteristic.

Further, a reed switch using the above-mentioned magnetic alloy and reed piece obtained by the manufacturing method of the present invention operates stably and accurately.

The alloy and lead piece manufactured by the manufacturing method of the present invention are also suitable for magnetic alloys that require square hysteresis characteristics in other electrical equipment.

Note that the alloys listed in Examples and Table 1 include Nb, Or, Mo, W, and Mn of relatively high purity.
, V, Ti.

Al, Si, rare earth elements, C, etc. were used, but instead of these, economically advantageous commercially available 7-Elements, or master alloys and Mitsushi metals could be used, but deoxidation and desulfurization would be sufficient during melting. If this is done, almost the same magnetic properties and workability as in the case of using these metals can be obtained.

Next, in the present invention, the composition of the alloy is 10% or less niobium,
A total of 0.0% of tantalum or less, 15% or less of molybdenum, and 20% or less of tungsten.
5-20%, vanadium 10% or less, chromium 25% or less, nickel 15% or less, @20% or less, cobalt 50%
Below, titanium 5% or less, zirconium 5% or less, hafnium 5% or less, silicon 5% or less, aluminum 5% or less,
Germanium 5% or less, gallium 5% or less, indium 5% or less, thallium 5% or less, tin 5% or less, antimony 5% or less, beryllium 8% or less, manganese 15% or less,
The reason for limiting the total content to 0.01 to 60% of one or more of the following: gold 10% or less, silver 10% or less, platinum group elements 5% or less, rare earth elements 6% or less, and carbon 0.5% or less As is clear from the examples and Table 1, the alloys in the composition range have a large residual magnetic flux density, exhibit excellent angular hysteresis, have a coercive force of 2 per cent or more, and are easy to process. This is because the magnetic alloy has stable magnetic properties even when heated at high temperatures, but if the composition falls outside this range, the magnetic properties deteriorate and processing becomes difficult, making it unsuitable as a rectangular hysteresis magnetic alloy.

Here, Nb, Ta, MO, W, V, O
r, Ni, Ou.

Co, Ti, Zr, Hf, Si,
Al, Ge, Ga, In.

Tj, Sn, St), Be, M,, n
, Au, Ag, platinum group elements, rare earth elements, and C have a particularly large effect of increasing the coercive force, 00 has a particularly large effect of increasing the residual magnetic flux density, and V, Nb, N
o, Ta, W, Ni, Ou.

Qo a Au e ) Lge Platinum group elements and rare earth elements have a particularly strong effect on improving squareness (, Ti,
SiA/, Get, Be, Mn, and rare earth elements have a particularly large effect of improving hot and cold workability, and MO2W, Or, Ni, Mn, and CO have a large effect of reducing the coefficient of thermal expansion.

The platinum group elements are palladium, platinum, and rhodium.

It consists of iridium, ruthenium, osmium and rhenium, and the rare earth elements are ythtrium, scandium, lanthanum, cerium and praseodymium.

It consists of neodymium, promethium, samarium, europium, gadolinium, terbium, dysprosium, holmium, erbium, thulium, ytterbium, and lutetium, all of which have similar effects.

Calcium, magnesium, strontium, barium, and boron have the effect of increasing workability, and calcium, bismuth, lead, tlA, sulfur-nitrogen, oxygen, and selenium have the effect of increasing coercive force and free machinability. It may be contained in a small amount as long as it does not impair the properties and workability of the invention alloy.

[Brief explanation of the drawing]

Fig. 1 is a diagram showing magnetic hysteresis loops with different angularity. Fig. 2 is a schematic diagram showing a conventional prismatic hysteresis magnetic alloy and a method for producing a lead piece. Fig. 8 A, B, and 0 are prismatic hysteresis loops of the present invention. FIG. 4, which is a schematic diagram illustrating a method for manufacturing a magnetic alloy and a reed piece, is a perspective view of a reed switch reed piece. Patent Applicant Institute of Electric and Magnetic Materials Foundation Figure 1 Figure 2 Procedural Amendment February 20, 1985 1, Case Description 1988 Patent Application No. 244714 2° Invention 0 Title Manufacture of prismatic hysteresis magnetic alloy Relation between the method of manufacturing the reed piece and the reed switch 3 and the case of the person making the amendment Patent applicant Institute for Electrical and Magnetic Materials 1, page 19 of the specification, line 4, ``correction'' was replaced with ``correction'' ,
” he corrected. 2, page 19, line 12 of [alloy number 1g (Fe-90
%. Manufacture of Ta-5%, Ou-5%) alloys and lead pieces.'' 3. Correct page 21, line 8 to read "0o-14%) alloy and lead piece production." 4, page 22, line 5 [alloy number 28 (Fe-70%
. Manufacturing of lead pieces (W-15%, Go-15%)" is corrected. 5. In the same page 26, line 19, “limited to 60%” was changed to “6
"We limited it to 0% and the remaining iron."

Claims (1)

[Claims] 1 Niobium 10 in weight ratio! %' or less, tantalum 20%
Below, molybdenum 15% or less and tungsten 20%
A total of 0.5 to 20% of one or more of the following:
Vanadium 10% or less, Ripm 25% or less, Nickel 1
5% or less, copper 20% or less, cobalt 50% or less, titanium 5% or less, zirconium 5% or less, hafnium 5% or less, silicon 5% or less, aluminum 5% or less, germanium 5% or less, gallium 5% or less, indium 5% or less, thallium 5% or less, tin 5% or less, antimony 5% or less, beryllium 8% or less, manganese 15% or less, gold 10% or less, Alo% or less, platinum group elements 5% or less, rare earth elements 5
% or less and carbon 0.5% or less, totaling 0.01 to 60%, the balance is iron, and a small amount of impurities is subjected to the first heat treatment after solution treatment.
It is characterized by heating at a temperature of 0 to 900°C, then cold working at a processing rate of 50% or more, and then heating this at a temperature of 500'' to 1000°C as a second stage heat treatment. A method for manufacturing a square hysteresis magnetic alloy. A total of 0.5 to 20% of one or more of 10% or less of niobium, 20% or less of tantalum, 15% or less of molybdenum, and 20% or less of tungsten, and vanadium. 10% or less, 25% or less, di-dityl 15
% or less, copper 20% or less, cobalt 50% or less, titanium 5
% or less, zirconium 5% or less, hafnium 5% or less,
Silicon 6% or less, aluminum 5% or less, germanium 5
% or less, gallium 5% or less, indium 5% or less, thallium 5% or less, tin 5% or less, antimony 5% or less, beryllium 3% or less, manganese 15% or less, gold 10% or less,
:, solution 1a% or less, platinum group elements 5% or less, rare earth elements 5
% or less and carbon 0.5% or less, a total of 0.01 to 60% of two or more types, the balance iron, and a small amount of impurities. processing, then the first stage heat treatment is 400 to 900
A method for producing a rectangular hysteresis magnetic alloy, which comprises heating at a temperature of 500°C to 1000°C as a second stage heat treatment. &・Niobium 10% or less, tantalum 2010% by weight
Below, molybdenum 15% or less and tungsten 20%
A total of 0.5 to 20% of one or more of the following:
Vanadium 10% or less, chromium 25% or less, nickel 1
5% or less, copper 20% or less, cobalt 50% or less, titanium 5% or less, zirconium 5% or less, hafnium 5% or less, silicon 5% or less, aluminum 5% or less, germanium 5% or less, gallium 5% or less, indium 5% or less, thallium 5% or less, tin 5% or less, antimony 5% or less, beryllium 8% or less, manganese 15% or less, gold 10% or less, silver 1.10% or less, platinum group elements 5% or less, rare earth elements An alloy consisting of 0.01 to 60% of one or more types of 5% or less and 0.5% or less of carbon, the balance iron, and a small amount of impurities is subjected to cooling at a processing rate of 50% or more after solution treatment. Temperature processing is performed, and then the first stage heat treatment is carried out at a temperature of 400 to 90
After heating at a temperature of 0°C and further cold working with a processing rate of 50% or more, the second stage heat treatment is 500 to 1
A method for producing a rectangular hysteresis magnetic alloy characterized by heating at a temperature of 000°C. 4. A combination of one or more of niobium 1θ% or less, tantalum 20% or less, molybdenum 15% or less, and tungsten 20% or less in weight ratio,
Vanadium 10% or less, chromium 25% or less, nickel 1
5% or less, silver 20% or less, cobalt 50% or less, titanium 5% or less, zirconium 5% or less, hafnium 6% or less, silicon 5% or less, aluminum 6% or less, germanium 5% or less, gallium 5% or less, indium 5% or less, thallium 3% or less, tin 5% or less, antimony 5% or less, beryllium 8% or less, manganese 15% or less, gold 10% or less, silver 10% or less, platinum group elements 5% or less, rare earth elements 5%
After solution treatment, an alloy consisting of one or more types of O, Oi ~ 60% of the following and 0.5% or less of carbon, the balance iron, and a small amount of impurities is subjected to the first heat treatment at 400%
After heating at a temperature of ~900°C and then cold working at a processing rate of 50% or more, it is formed into a lead piece, which is then further heated at a temperature of 500 to 1000°C as a second stage heat treatment. Characteristic lead piece manufacturing method. 6 A total of 0.5 to 20% of one or more of niobium 10% or less, tantalum 20% or less, molybdenum 15% or less and tungsten 20% or less, vanadium 10% or less, and tungsten 0.5 to 20% by weight % or less, nickel 16%
Less than 20% copper, less than 50% cobalt, 6% titanium
Below, zirconium 5% or less, hafnium 5% or less, silicon 5% or less, aluminum 5% or less, germanium 5% or less
The following: gallium 5% or less, indium 5% or less, thallium 5% or less, tin 6% or less, antimony 5% or less, beryllium 8% or less, manganese 15% or less, gold 10% or less, silver 10% or less, platinum group elements 5% or less, rare earth elements 5% or less, and carbon 0.5% or less, a total of 0.01 to 60% of one or more of them, the balance being iron, and a small amount of impurities processed after solution treatment. After cold working at a rate of 50% or more and then forming into a lead piece, it is heated at a temperature of 400 to 900°C as a first stage heat treatment, and further heated at a temperature of 500 to 1000 °C as a second stage heat treatment. A method for manufacturing a lead piece, characterized by: 6. A total of 0.5 to 20% of one or more of 10% or less niobium, 20% or less tantalum, 15% or less molybdenum, and 20% or less tungsten, 10% or less vanadium, and 25% chromium by weight. Below, nickel 15
% or less, copper 20% or less, cobalt 50% or less, titanium 5
% or less, zirconium 5% or less, hafnium 5% or less,
Silicon 5% or less, aluminum 5% or less, germanium 5
% or less, gallium 5% or less, indium 5% or less, thallium 5% or less, tin 5% or less, antimony 5% or less, beryllium 8% or less, manganese 15% or less, gold 10% or less,
Silver: 10% or less, platinum group elements: 5% or less, rare earth elements: 5%
An alloy consisting of 0.01 to 60% of one or more of the following and 0.5% or less of carbon, the balance iron, and a small amount of impurities is subjected to cold working of 50% or more after solution treatment. The lead is then heated at a temperature of 400 to 900°C as a first stage heat treatment and then formed into a reed piece, which is further heated at a temperature of 500 to 1000 °C as a second stage heat treatment. Method of manufacturing pieces. ? , 10% or less of niobium, 20% or less of tantalum, 15% or less of molybdenum, and 20% or less of tungsten, or a total of 0.5 to 20% of two or more, by weight;
Vanadium 10% or less, chromium 25% or less, nickel 1
5% or less, copper 20% or less, cobalt 50% or less, titanium 5% or less, zirconium 5% or less, hafnium 5% or less, silicon 5% or less, aluminum 5% or less, germanium 5% or less, gallium 5% or less, indium 5% or less, thallium 5% or less, tin 5% or less, antimony 5% or less, beryllium 8% or less, manganese 15% or less, gold 10% or less, silver, 10% or less, platinum group elements 5% or less, rare earth elements 5
% or less and carbon 0.5% or less, a total of 0.01 to 60% of two or more types, the balance iron, and a small amount of impurities. After solution treatment, cold working with a processing rate of 50% or more. processing, then the first stage heat treatment is 400 to 900
The lead piece is heated at a temperature of °C and then subjected to cold working at a processing rate of 50%, further formed into a lead piece, and then heated at a temperature of 500 to 1000 °C as a second stage heat treatment. Manufacturing method. & A total of 0.5 to 20% of one or more of 10% or less niobium, 20% or less tantalum, 15% or less molybdenum, and 20% or less tungsten, 10% or less vanadium, and 25% tungsten by weight. % or less, nickel 15%
Less than 20% copper, less than 50% cobalt, 5% titanium
Below, zirconium 5% or less, hafnium 5% or less, silicon 5% or less, aluminum 5% or less, germanium 5% or less
The following: gallium 5% or less, indium 5% or less, thallium 5% or less, tin 5% or less, antimony 5% or less, beryllium 8% or less, manganese 15% or less, gold 10% or less, silver 10% or less, platinum group elements 5% or less, rare earth elements 5% or less, and carbon 0.5% or less, a total of 0.01 to 60% of 1a or two or more types, the balance iron, and a small amount of impurities. Processing rate after solution treatment. After applying cold working of 50% or more and then forming it into a lead piece, b6 (0~1000°
A method for producing a reed piece, characterized by heating at a temperature of C. 9. A reed switch made of a rectangular hysteresis magnetic alloy that has a large residual magnetic flux density, a rectangular hysteresis characteristic with excellent angularity, and is easy to forge and process. 10. A reed switch consisting of a reed piece that has a high residual magnetic flux density and a rectangular hysteresis characteristic with excellent angularity.