JPS58136739A - Rapidly cooled magnet alloy and its manufacture - Google Patents

Abstract

PURPOSE:To manufacture a magnet alloy with superior magnetic characteristics by spraying a molten alloy having a restricted composition consisting of Sm and Fe or further contg. Co on a rotating body in vacuum or an inert gaseous atmosphere to rapidly cool the alloy. CONSTITUTION:An alloy consisting of, by weight, 45-92% Sm and 8-55% Fe or further contg. 0.1-47% Co is melted in a crucible made of quartz or the like by high frequency heating or other method, and by applying pressure with Ar or the like, the molten metal is sprayed on a rotating body such as a roll or a disk having 2.5-30m/sec surface speed in vacuum or an atmosphere of an inert gas such as Ar from the bottom molten metal outlet of the crucible to obtain a ribbonlike magnet alloy by rapid cooling. In order to further improve the magnetic characteristics of the resulting magnet alloy, the alloy is heat treated at a relatively low temp. such as 200-600 deg.C for 0.5-7hr in vacuum or an inert gaseous atmosphere preferably in a magnetic field having <=15,000Oe.

Description

[Detailed description of the invention]

The present invention has a rapid cooling hardness of 1141 yen? The present invention relates to Ei alloys, and more particularly to rapidly solidified magnet alloys obtained from Sw+ -Fe and Sm -Fe-Co alloy compositions and methods for producing the same. Conventionally, 5111 was used as a rare earth magnet alloy containing rare earth elements.
Metal open compound magnets represented by C05, 5IIICO7, 5II12COI7, etc. are known. Because these rare earth magnets C and L have excellent magnetic properties,
Currently widely used. In general, the manufacturing method for rare earth magnets requires melting, crushing, press forming, and sintering temporary heat treatment in order to obtain excellent magnetic properties, and temperature control is extremely complicated. Therefore, it has drawbacks such as being brittle and having extremely poor mechanical processing TM. The present invention has been made to improve this problem, so Sm4
5-92 wt%, Fe 8-55 wt% or S
m 45"-92wt%, l'me 8=-55Wj
%, CO0.1 to 47 wt%, and is characterized by being rapidly cooled from a molten metal, and a method for producing the same. The rapidly cooled magnetic C7 alloy of the present invention is different from the conventional rare earth C7 alloy.
It composition and metal phase are completely different, and the alloy obtained with - is Sm -1-8m [c 2 , Sm FO2,
Sm Fc 21-8m Fe 3 , Sm -1-5
m (re. Co) 2 , 8111 (Fe, Go) 2
It consists of any intermetallic compound represented by +3m (1-e. C0)3 or a two-phase mixture of metal-1 intermetallic compounds. The heat treatment to improve the magnetic properties of the quenched magnet alloy does not require heat treatment at a high temperature like that of conventional rare earth cobal 1-based sintered magnets. It is characterized by obtaining a magnetic alloy of. This is clear from the following test. Various Sm-Fe and Sm-Fe-Co alloys were obtained by high-frequency melting or arc melting. This alloy is a polycrystalline alloy, and when the compounds were identified by powder X-ray diffraction method, these alloys 4. tSm, 81
11 Fe 2 , Sm (Fe, C0) 2, SmF
(!3, Sm (FQ, Co) It is identified as an alloy of 4T from a single element represented by (FQ, Co)3, an intermetallic compound, two types of intermetallic compounds, and a single intermetallic compound.The magnetic properties of these alloys were determined at room temperature. When measured using a $31 oscillating magnetic force probe, the coercive force (dk) was about 3!
It is about 0 to 50 (emu/a). In addition, even when this bulk polycrystalline alloy is subjected to heat treatment methods such as a combination of steps, cooling, or holding at a constant temperature for a certain period of time for the purpose of improving magnetic properties, the improvement in +tk and σ values is extremely small. However, there is little hope for using rare earth magnets based on their magnetic properties or single-stroke properties. By quenching the material according to the present invention, it can be made into a material superior to that of magnetic 14 bamboo. Next, the reasons for limiting the scope of the claims of the present invention will be described. First, if the darkness of the rare earth element Srn in C3 in the 3m-[e alloy is less than 45 wt%, the value power': 1000 (0(i)
It becomes below. In addition, if the Sn+ opening exceeds 92 wt%, the 5] seventh value will be extremely reduced, and the rare earth element opening will be extremely large. In the case of 1°F e, which has disadvantages such as difficulty in rapidly solidifying magnet alloys having a shape of 19%, the saturation magnetization σ (medium low 11%) is less than 8 wt% or exceeds LL55w1%. This is a major drawback in that a quenched magnet alloy with excellent magnetic properties cannot be obtained. In the case of Sm-FO-GO alloy, the lower limit of Fe is 8 wt%, and if it is less than 8 wt%, Table 1 and the saturation magnetization σ value will be low, making it impossible to obtain a rapidly solidified magnet alloy with excellent magnetic properties. . 5- When CO exceeds 47W1%, the IW value of the rapidly solidified magnet alloy becomes extremely low. The method for producing a rapidly solidified magnetic alloy of the present invention is performed by
The liquid quenching method is used to inject the molten metal into a ribbon-like sample. In the liquid quenching method, raw materials or alloys of constituent elements are charged into a crucible made of quartz, oxide, or high melting point metal, melted by high frequency or resistance heating, and then Δr Gas injection pressure 0.1=
It is quenched on the surface of a metallic rotating body at 1 kg/cm2 to obtain a ribbon-shaped magnetic alloy. All of these melting and injection operations must be performed in an atmosphere of an inert gas such as Ar or nitrogen gas in order to prevent oxidation of the rare earth elements. The material of the rotating body for rapidly cooling the molten metal can be Cu, l':e and its Cr plating, heat-resistant and contact-resistant alloys such as stainless steel, or ceramics. In consideration of the

[! It is best to use a lamic surface treatment. The shape of the rotating body may be a square, a disk, or the like, and the molten metal may be injected into the inner surface of a cylinder. The quenched magnet alloy of the present invention is characterized in that the magnetic properties of the magnet alloy obtained by cooling at a high speed rotating body, e.g. The surface speed of the rotating body is 2.5 to 3.
0 n+ /sec. For example, in the case of a rotating roll, the surface speed of this rotating body is the circumference of the roll ×
It is defined by the number of rotations (r. 0, m). The ribbon thickness of the ribbon-shaped magnet alloy obtained when the surface speed of the rotating body is 2.5 to 30 m/sec is about 10 to several hundred IT III, but when the surface speed of the rotating body is 30 m/sec, If it exceeds this, the thickness of the ribbon becomes extremely thin and it becomes difficult to produce 1q of high quality continuous long ribbons. Since the rapidly solidified magnet alloy IJM band obtained from these manufacturing methods is suitable for thin plate-shaped hard magnetic magnets, it requires less time in the manufacturing department compared to the method of cutting sintered magnets. Significant increase in the number of culms (in addition to simplification, mechanical processing and cutting can be used to commercialize the product) -
He is also right-handed. It is also advantageous in that it can improve magnetic properties without requiring heat treatment at high temperatures. Details of the present invention are explained in detail in Sogogo by Examples v2 #I ”l
−'ru. Example 1 An ingot with a composition of 8 m 68.78% and 1 e 31.22% was injected into a Cu roll using a Δr gas of 0.4 kg/a1. Figure 1 shows the magnetic properties of the rapidly solidified magnetic alloy obtained in the above. The magnetism of the alloy as it is quenched depends on the surface speed of the rotating roll, and when the surface speed is about 8 m/sec (7) It:
+) k: approximately 2100 (Oe
). From the figure, the magnetic properties of the magnet alloy in the rapidly cooled 1=as-is state are as follows: The surface speed of the rotating roll is approximately 8 m/s.
When it is smaller than ea, [7] was found to decrease rapidly. However, the change in IHc at a surface velocity of 8 m/sec or higher is gradual, about 8 to 1! lm/s
Since it is only necessary to adjust to ec, manufacturing becomes easy. Powder X-ray diffraction of this rapidly solidified magnetic alloy does not show a complete halo pattern as is generally observed in amorphous materials, but instead shows a diffraction peak intensity that depends on the rotating roll surface speed. When measured under the conditions of C0Kct+ with an accelerating voltage of 50 KV and a filament current of 160 mA, the surface velocity was approximately 2.
In the case of 2 m/sec, diffraction lines showing a small peak intensity are superimposed on the halo pattern. Furthermore, for the surface velocity of about 411/see, which has an extremely low surface velocity, it shows a larger peak intensity than that of 22 tn/sec, and the diffraction lines appear more frequently. Peak intensity and VA of i!
lf shows that the magnetism of the quenched magnetic Ei alloy of the present invention depends on the rotating roll surface speed, and the alloy exhibits amorphous properties when the surface IR degree is large, but when the surface speed is small, I learned that crystalline alloys become dominant. When an attempt was made to identify the substance from the diffraction line, -b of about 9-22 m/Sec was unclear. However, when the shielding is maximum at about Bm/sec, 5Ill
A substance that appears to be Fez and η5Ill, which exhibits an extremely small peak intensity, was identified. Surface speed is approximately 4m/sea
In this case, diffraction lines of Sm and 5ill Fe2 appeared at similar frequencies, and it was presumed to be a two-phase mixture of 5ill+5illFe2. From this, it seems that the intermetallic compound 5IIIFc2 is the main factor in producing excellent magnetic properties in the rapidly solidified magnet alloy 5 alloy of the present invention. By the way, the intermetallic compounds in the 5III-Fe binary alloy include Sm Fe 2 , Sm Fe 3 , Sm
The existence of Fe 5 and Sm 2 [C17 is known. Although these intermetallic compounds are magnetically excellent materials, they have a k of about 350 (Qe) or less using normal manufacturing methods, and cannot be used as practical magnets. It is also known that 5lll is non-magnetic at room temperature. However, 5IR68 obtained by the 'IIJ manufacturing method of the present invention
, 78%, Fe31.22% is recognized from the figure.
− +lk of bulk crystals with the same composition is 1/
It shows only about 200 (Oe) of 10. Example 2 S +n 63.90%, Fe 28.56%, CO7
An alloy having a composition of 2'% was prepared in the same manner as in Example 1, and the magnetic properties of the quenched magnet alloy are shown in Figure 2. This t
The IW of gold has a rotational surface speed of about 16II1.
．． /seC, the highest roar, part 1 "I is about 2200 (O
e). When powder X-ray diffraction was attempted using this rapidly solidified magnetic alloy, it was found that the above-mentioned 3m68.78% and e31
．． The diffraction pattern is similar to that of 22% b. This can be inferred from the fact that the Fe-C0 alloy is completely solid and liquid.31 Rapid cooling with a surface velocity of about 8 m/sec! &Right gold alloy, Sm (F(!, Co)2 seems to be Sm with extremely weak peak intensity, and CO was not detected.Also, the primary concentration of a block alloy with the same composition at room temperature is 210 (Oe). According to the production method 7j of the present invention, INc is 2200
(Oe,) It was found that this alloy did not exhibit an IW that was about 10 times better than that of the rapidly solidified magnet alloy. Example 3 About the S m-F' e-Co alloy of the present invention
l (F e −Go ) 2 to 3 m (Fe
An experimental example of C is shown for the components between , Co )3. S
m53.30%, Fe36. OFi%, CO9,75%
Invoice 1~ is 8111 (FO, Co) 2
Consisting of a two-phase mixture of +8m (Fc, C0)3,
The & of this alloy at room temperature is about 250 (Oc). A quenched magnet alloy was made from this alloy by the manufacturing method of the present invention, and the surface speed of the rotating roll was approximately 24.16.8.4.
m/sec, each minister is 2000.15
00.1600.1850 (Oe). As a result of powder X-ray diffraction with a surface velocity of about 4 III /Sec,
Although the intensity of each diffraction line is extremely small when compared with that of polycrystalline No. 5, the content of these lines is presumed to be Sm(Fe.C0)2 and 8111(Fe,Go)3. As a result, 5lll (Fe, Go
It is also possible to produce rapidly solidified magnet alloys with excellent IW in the present invention for components between >2 and Sm (Fe 2 , . . . , Go 2 ) 3 . Example 4 Next, an experimental example regarding components near the intermetallic compound 5IIIFe3 will be shown. 3m39.96%, l:647.50%
, Co 12.53% has a +lk of about 1900 (Oe) when the rotating roll surface speed is about 24 m/sea. +l of polycrystalline alloy with the same composition
k is about 200 (Oe), and the present invention makes it possible to produce a rapidly solidified magnetic alloy with excellent properties. Example 5 A similar experiment was conducted in the case of an Sm--Fe alloy, and the results are shown in Table 1 and FIG. 3. In Table 1, the alloy composition formula 5lll+-xFe, 0.4≦x'io, 6 is used to indicate the component A. =13-Table 1 Figure 3 shows the case where the rotating roll surface speed is about 24 m/sec. From the figure, the magnetic properties of the rapidly solidified magnet alloy are about 1000-2000 (Oe), and the U IOK is about 10-40 (emu/IJ). Note that II&: of a polycrystalline alloy having the same composition is approximately 200 to 300 (Oe). Example 6 The compositional formula and components of the Sm-Fe-Goo alloy are shown in Tables 2 and 3.
I-Y COv>. , r(-10, 2≦Y≦ 1.0
Table 3 shows Sm +-x (Fe,
,yco,,, ). , 0.2≦8≦0.8. The manufacturing conditions were the same as in Example 1, except that the rotating rolls were made of iron (14 mm). Figure 4 shows S 11111. +ILJ-(FO+-v
Regarding the magnetic properties of the rapidly solidified magnetic alloy shown by the composition formula of COY) aFz, the rotating roll surface speed is 16 m/sec.
The case is shown below. From the figure, as the value of Y increases, that is, as the content of CO increases, the +lk and aIOK values gradually decrease. Note that a polycrystalline material with the same composition has a reed of about 250□-350 (OQ) and a IOK of about 1 () to -40 (emulo). Figure 5 shows S III I-X (F ea, g Go
a, z) The magnetic properties of the rapidly solidified magnet alloy shown by the composition formula of X are shown. The rotational surface velocity is approximately 16 Ill/SeC. From the figure, the x plant where & is the maximum has approximately o, sr, and in this case Ilk is approximately 2600
(00), σ is approximately 52 (emu 10 ). In order to produce a quenched magnetic alloy having a strong magnetic property, X must be in the range of 0.2≦X≦0.8. In addition, & of polycrystalline ones with the same components is approximately 200-, 300 (
Oe), (7ox is approximately 10-60 (emLI/11)
It is. As described above, according to the present invention, polycrystalline alloys with 11&: of about 200-350 (Oe) can also be treated.
T17- +Ik is about 2600 (Oe) (7) value to the right
Le? It is possible to produce a cold 1i Ui gold alloy.

[Brief explanation of the drawing]

FIGS. 1 and 2 are graphs showing the relationship between rotation [1 and surface velocity]. 3 to 5 are graphs showing the relationship between the composition and the &73 and σIOK values. Special Da 1 Applicant Mitsubishi Steel Corporation Agent Patent Attorney Hidetake Komatsu 18- ('/Ijun〕') (n0)'7/J (rau+su1alD (>o) n(4z (hekuno7H')

Claims (1)

[Claims] 1. Samarium (Sm) 45-92 wt%, iron (
A rapidly solidified magnetic alloy comprising 8 to 55 wt% of Fe), characterized in that it is rapidly cooled from a molten metal. 2. Samarium (SIR) 45-92 wt%, iron (
Fc) 8-55W [%, cobalt (GO) 0.1-47
A quenched magnetic alloy characterized in that it is composed of 50% by weight or less and is rapidly cooled from a molten metal. 3.Samarium (Sm) 45-92%, iron (Fe) 8
A molten alloy consisting of ~55 wt% was heated at a surface velocity of 2.5.
A method for producing a rapidly solidified magnetic alloy, which comprises injecting into a rotating body of ~30 m/SeC, F, in a vacuum or an inert gas atmosphere, and rapidly cooling it. 4. Samarium (Sm) 45~! J2 wt%. Iron (Fe) 8~55 wt%, cobalt (co) 0.1~
A molten alloy consisting of 41W [%] has a surface velocity of 2.5%.
~30 m/SeG rotating body - Method 5 for producing a rapidly cooled magnetic alloy characterized by injecting and rapidly cooling in a vacuum or an inert gas atmosphere. A method for producing a rapidly solidified magnet alloy according to claim 3 or 4, which comprises heat treatment in a vacuum or inert gas atmosphere for 5 to 7 hours. 6. The method for producing a rapidly solidified magnet alloy according to claim 5, wherein the heat treatment is carried out in a magnetic field of 15,000 oersted or less.