JPH0252413B2 - - Google Patents
Info
- Publication number
- JPH0252413B2 JPH0252413B2 JP56164826A JP16482681A JPH0252413B2 JP H0252413 B2 JPH0252413 B2 JP H0252413B2 JP 56164826 A JP56164826 A JP 56164826A JP 16482681 A JP16482681 A JP 16482681A JP H0252413 B2 JPH0252413 B2 JP H0252413B2
- Authority
- JP
- Japan
- Prior art keywords
- zirconium
- less
- permanent magnet
- intermetallic compound
- metal
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Lifetime
Links
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 59
- 229910052726 zirconium Inorganic materials 0.000 claims description 58
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 claims description 52
- 229910052742 iron Inorganic materials 0.000 claims description 31
- 239000010949 copper Substances 0.000 claims description 30
- 229910052684 Cerium Inorganic materials 0.000 claims description 28
- 229910052802 copper Inorganic materials 0.000 claims description 27
- 229910017052 cobalt Inorganic materials 0.000 claims description 25
- 239000010941 cobalt Substances 0.000 claims description 25
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 claims description 25
- 229910052751 metal Inorganic materials 0.000 claims description 25
- 239000002184 metal Substances 0.000 claims description 25
- 229910000765 intermetallic Inorganic materials 0.000 claims description 23
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 22
- 229910052772 Samarium Inorganic materials 0.000 claims description 17
- 229910052761 rare earth metal Inorganic materials 0.000 claims description 17
- KZUNJOHGWZRPMI-UHFFFAOYSA-N samarium atom Chemical compound [Sm] KZUNJOHGWZRPMI-UHFFFAOYSA-N 0.000 claims description 17
- 239000013078 crystal Substances 0.000 claims description 15
- 150000002910 rare earth metals Chemical class 0.000 claims description 14
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 12
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 6
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 6
- 229910052804 chromium Inorganic materials 0.000 claims description 6
- 239000011651 chromium Substances 0.000 claims description 6
- 229910052735 hafnium Inorganic materials 0.000 claims description 6
- VBJZVLUMGGDVMO-UHFFFAOYSA-N hafnium atom Chemical compound [Hf] VBJZVLUMGGDVMO-UHFFFAOYSA-N 0.000 claims description 6
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 claims description 6
- 229910052759 nickel Inorganic materials 0.000 claims description 6
- 229910052758 niobium Inorganic materials 0.000 claims description 6
- 239000010955 niobium Substances 0.000 claims description 6
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 6
- 229910052715 tantalum Inorganic materials 0.000 claims description 6
- GUVRBAGPIYLISA-UHFFFAOYSA-N tantalum atom Chemical compound [Ta] GUVRBAGPIYLISA-UHFFFAOYSA-N 0.000 claims description 6
- 229910052719 titanium Inorganic materials 0.000 claims description 6
- 239000010936 titanium Substances 0.000 claims description 6
- 229910052720 vanadium Inorganic materials 0.000 claims description 6
- GPPXJZIENCGNKB-UHFFFAOYSA-N vanadium Chemical compound [V]#[V] GPPXJZIENCGNKB-UHFFFAOYSA-N 0.000 claims description 6
- 150000002739 metals Chemical class 0.000 claims description 4
- ZMIGMASIKSOYAM-UHFFFAOYSA-N cerium Chemical compound [Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce] ZMIGMASIKSOYAM-UHFFFAOYSA-N 0.000 claims 12
- 229940126062 Compound A Drugs 0.000 claims 2
- NLDMNSXOCDLTTB-UHFFFAOYSA-N Heterophylliin A Natural products O1C2COC(=O)C3=CC(O)=C(O)C(O)=C3C3=C(O)C(O)=C(O)C=C3C(=O)OC2C(OC(=O)C=2C=C(O)C(O)=C(O)C=2)C(O)C1OC(=O)C1=CC(O)=C(O)C(O)=C1 NLDMNSXOCDLTTB-UHFFFAOYSA-N 0.000 claims 2
- 229910052738 indium Inorganic materials 0.000 claims 1
- 239000000047 product Substances 0.000 description 20
- 230000032683 aging Effects 0.000 description 16
- 238000010438 heat treatment Methods 0.000 description 14
- 239000000203 mixture Substances 0.000 description 14
- GWXLDORMOJMVQZ-UHFFFAOYSA-N cerium Chemical compound [Ce] GWXLDORMOJMVQZ-UHFFFAOYSA-N 0.000 description 11
- 238000001816 cooling Methods 0.000 description 11
- 229910017827 CuâFe Inorganic materials 0.000 description 10
- 230000004907 flux Effects 0.000 description 9
- 238000004881 precipitation hardening Methods 0.000 description 9
- 238000011282 treatment Methods 0.000 description 9
- 230000007423 decrease Effects 0.000 description 8
- 230000000694 effects Effects 0.000 description 7
- 239000000463 material Substances 0.000 description 7
- 239000000523 sample Substances 0.000 description 7
- 238000000034 method Methods 0.000 description 6
- 239000000843 powder Substances 0.000 description 6
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 4
- 238000012360 testing method Methods 0.000 description 4
- 229910045601 alloy Inorganic materials 0.000 description 3
- 239000000956 alloy Substances 0.000 description 3
- 238000002844 melting Methods 0.000 description 3
- 230000008018 melting Effects 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 229910004625 CeâZr Inorganic materials 0.000 description 2
- 229910052786 argon Inorganic materials 0.000 description 2
- 230000008901 benefit Effects 0.000 description 2
- 230000005347 demagnetization Effects 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 230000001590 oxidative effect Effects 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 230000008569 process Effects 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 238000005245 sintering Methods 0.000 description 2
- 229910020598 Co Fe Inorganic materials 0.000 description 1
- 229910002519 Co-Fe Inorganic materials 0.000 description 1
- 229910002520 CoCu Inorganic materials 0.000 description 1
- 229910001021 Ferroalloy Inorganic materials 0.000 description 1
- 101000993059 Homo sapiens Hereditary hemochromatosis protein Proteins 0.000 description 1
- 238000000441 X-ray spectroscopy Methods 0.000 description 1
- IIMKXPCVINVTJV-UHFFFAOYSA-N [Ce].[Sm].[Co] Chemical compound [Ce].[Sm].[Co] IIMKXPCVINVTJV-UHFFFAOYSA-N 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 230000005540 biological transmission Effects 0.000 description 1
- 230000001364 causal effect Effects 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 238000004891 communication Methods 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 238000000635 electron micrograph Methods 0.000 description 1
- 238000002149 energy-dispersive X-ray emission spectroscopy Methods 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 238000003331 infrared imaging Methods 0.000 description 1
- 230000002427 irreversible effect Effects 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 230000002441 reversible effect Effects 0.000 description 1
- 229910000938 samariumâcobalt magnet Inorganic materials 0.000 description 1
- 238000001878 scanning electron micrograph Methods 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
Classifications
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/032—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials
- H01F1/04—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials metals or alloys
- H01F1/047—Alloys characterised by their composition
- H01F1/053—Alloys characterised by their composition containing rare earth metals
- H01F1/055—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5
Landscapes
- Chemical & Material Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Inorganic Chemistry (AREA)
- Engineering & Computer Science (AREA)
- Power Engineering (AREA)
- Hard Magnetic Materials (AREA)
Description
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ãApplied Physics Lettersã第30å·»ãNo.12ã第
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Proceeding of the Fourth International
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The present invention relates to rare earth cobalt magnets, and more specifically, the present invention relates to rare earth cobalt magnets, and more specifically, the present invention relates to rare earth cobalt magnets.
This invention relates to the improvement of Ce-Sm-Co-Cu-Fe precipitation-hardening permanent magnets, which are mainly composed of Fe-based and cerium-samarium-cobalt intermetallic compounds. Precipitation hardening rare earth cobalt magnets that use cerium as the rare earth element are superior in terms of resources and raw material costs compared to conventional SmCo 5 magnets that use large amounts of expensive samarium and cobalt, and are industrially viable. Although it has been attracting attention, its magnetic properties have been insufficient from a practical point of view. For example, June 1977 "Applied Physics Letters" Volume 30, No. 12, No.
According to the description on pages 669 to 670 or the description in Japanese Patent Publication No. 56-39375, the maximum energy product (BH) of the Ce-Co-Cu-Fe system nax is 13MGOe the residual magnetic flux density B r is
It can be seen that the coercive force iHc was about 7 kG and about 6100 to 6900 Oe, and the composition was oriented to 9% or more copper and 12% or less iron. Furthermore, CeâSmâCoâ in which part of cerium was replaced with samarium
For example, regarding Cu-Fe precipitation hardening permanent magnets,
Proceeding of the Fourth International
Workshop on Rare earth Cobalt Permanent
According to Magnets (1979 5#), Co/Ce
Maximum energy product (BH) near +Sm=0.5 nax
It can be seen that 19 MGOe and coercive force iHc of about 7000 Oe were obtained, and the composition was oriented to 9% or more copper and 12% or less iron. In these precipitation hardening type magnets, the copper-containing phase exhibits a fine cell structure and improves the coercive force, so a relatively high copper content is desired from the viewpoint of maintaining the coercive force. In addition, the iron content is also low from the viewpoint of coercive force. The object of the present invention is to
Compared to conventional magnets, Fe-based and Ce-Sm-Co-Cu-Fe-based permanent magnets maintain high coercive force even in compositions with low copper content and high iron content. By taking advantage of the high residual magnetic flux density, which is an advantage of a low Cu and high Fe composition, it has excellent magnetic properties of both maximum energy product and coercive force, and also uses inexpensive cerium as the main rare earth element. Our goal is to provide permanent magnets. In addition to the cell structure of the Cu-containing phase seen in the microstructure of conventional precipitation-hardened magnets, the present invention precipitates a zirconium-containing phase parallel to the c-plane of the crystal of a rare earth cobalt intermetallic compound containing cerium as an essential component. In addition to the domain wall pinning effect due to the cell boundaries of the copper-containing phase, the domain wall pinning effect due to the zirconium-containing phase is added, and a high coercive force is maintained even at low copper content and high iron content. At the same time, a high maximum energy product is possible. As a result of intensive research, the present inventor discovered a series of heat treatments that precipitate zirconium-containing phases parallel to the c-plane of the crystals of the intermetallic compound, and confirmed the causal relationship between the spacing between the zirconium-containing phases and magnetic properties. This completes the present invention. That is, the present invention has a weight percentage of 20 to 20%.
30% cerium, 3 to 9% copper, 1 to 5
% zirconium and 10 to 30% iron, the balance being cobalt, and a permanent magnet comprising an intermetallic compound mainly composed of rare earth cobalt, in which zirconium is parallel to the c-plane of the crystal of the intermetallic compound. It is characterized in that the contained phases exist with an average spacing of 5000 Ã
or less. In the present invention, the magnetic field is parallel to the c-plane of the crystal, which did not exist in conventional Ce-Co-Cu-Fe system and Ce-Sm-Co-Cu-Fe system precipitation hardening permanent magnets. Due to the precipitated zirconium-containing phase, in the former system, the coercive force iHc is 4000 Oe or more, preferably 7000 Oe or more, and the maximum energy (BH) nax
Sm
When the ratio of (%)/Ce (%) + Sm (%) is 0.5,
This enables a high coercive force and maximum energy product represented by a coercive force iHc of 12000 Oe or more and a maximum energy product (BH) of nax 23 MGOe or more. However, if the average interplanar spacing of the zirconium-containing phase parallel to the c-plane of the crystal of the intermetallic compound exceeds 5000 Ã
, the magnetic properties will not be much different from those of the conventional precipitation hardening type permanent magnet, so 5000 Ã
is the upper limit. There is. This preferred average spacing is 2000 Ã
or less. In the permanent magnet of the present invention, the cerium content is
When the copper content is less than 20%, the copper content is less than 3%, or the iron content is more than 30%, the coercive force and the maximum energy product decrease. The cerium content exceeds 30%, the copper content exceeds 9%, or the iron content
If it is less than 100%, the residual magnetic flux density or the squareness of the demagnetization curve will decrease, and the maximum energy product will also decrease. If the zirconium content is less than 1%, the average spacing of the zirconium-containing phase will exceed 5000 Ã
even if the heat treatment of the present invention described below is performed, and no effect can be expected. On the other hand, if the zirconium content exceeds 5%, the residual magnetic flux density and Maximum energy product decreases. In the above composition, less than 28% cerium and 12% or more iron, which provides a high magnetic flux density, are particularly preferred. In the present invention, in addition to zirconium, at least one of hafnium, titanium, vanadium, niobium, and tantalum is added in a total amount of 1
% but not more than 5% (however, the lower limit of zirconium is 1
%), the same effect as when adding zirconium alone is produced. Further, when hafnium, titanium, vanadium, niobium, and tantalum are added alone, phases containing each element precipitate as in the case of zirconium, and the same effect can be expected. In addition, replacing 80% or less of cerium (not including 0) with samarium, that is, 0<Sm
It is also possible to add samarium to the permanent magnet in the relationship of (%)/Sm (%) + Ce (%)âŠ80%. When the above ratio exceeds 80%, expensive samarium increases, and the industrial value in terms of resources and raw material costs decreases. Furthermore, the same effect can be obtained even if part of the iron is replaced with 80% or less (not including zero) of one or more of manganese, nickel, and chromium.
When the amount of substitution exceeds 80%, the residual magnetic flux density decreases,
The maximum energy product also decreases. The precipitation hardening type permanent magnet of the present invention is a conventional Ce-Co permanent magnet.
- Compared to the Cu-Fe system or the Ce-Sm-Co-Cu-Fe system, temperature characteristics such as reversible temperature change in magnetic flux and irreversible demagnetization are significantly improved. Ce-Co-Cu-Fe system and Ce-Sm according to the present invention
The method for manufacturing the -Co-Cu-Fe precipitation hardening permanent magnet is as follows. First, raw metals are mixed in a desired ratio and alloyed by high-frequency melting in vacuum or in a non-oxidizing atmosphere. At this time, there is no problem in using the additive metal such as zirconium in the form of a ferroalloy. Furthermore, the melting may be performed by other methods, such as a resistance heating furnace, an infrared imaging furnace, an arc melting furnace, and the like. An ingot having a predetermined composition is coarsely pulverized using a stamp mill, a geocrusher, etc. to form an alloy powder. In the process up to this point, alloy powder may be obtained by a process such as a reduction diffusion method. The obtained alloy powder is further pulverized into particles having a size of about 3 to 6 Όm using a jet mill, an attritor, a ball mill, or the like. Thereafter, the fine powder is compression molded into a desired shape using a die press, isostatic press, etc. in a magnetic field. The above steps are not particularly different from conventional permanent magnet manufacturing methods. Hereinafter, a heat treatment is performed to precipitate a zirconium-containing phase. The molded body is sintered and simultaneously subjected to solution treatment at a temperature of 1000° C. to 1150° C. in a vacuum, a non-oxidizing atmosphere, or a reducing atmosphere, etc., and then rapidly cooled to a temperature of 950° C. or lower, for example, to room temperature. The solution-treated sintered body (in the case described above, sintering and solutioning are carried out in one step) is then subjected to isothermal aging at a temperature of 750°C to 900°C for at least 15 minutes, and then Cool to a temperature below 650°C at a rate of 10°C/min to 10°C/min. Further, it is slowly or gradually cooled from a temperature range of 500°C to 650°C to a temperature of 400°C or less at a cooling rate of 2°C/min or less. The permanent magnet of the present invention can be widely used in watches, electric motors, meters, communication devices, computer terminals, speakers, video disks, and various other parts. Example 1 Raw metals were blended and mixed to have a predetermined composition, and this mixed metal was melted by high frequency heating in argon gas to obtain an ingot. This ingot was coarsely ground with a stamp mill, and further finely ground with a jet mill to an average particle size of about 4 Όm. The obtained fine powder was sequentially compressed in a magnetic field, and the compacted body in the magnetic field was sintered in vacuum at a temperature of 1000 to 1150°C for 1 hour.
Container treatment, then quenching to room temperature with argon gas, further isothermal aging in the temperature range of 750 to 900°C for 15 minutes or more, and then cooling to 600°C at a rate of 2°C/min to 10°C/min. Then, the sample was gradually cooled down to 300°C at a cooling rate of 1°C/min. The coercive force, residual magnetic flux density, and maximum energy product of each sample material are shown in each drawing. The percentages of the sample material powder shown below are weight percentages. (1) Composition of 7% Cu, 14% Fe, 2.4% Zr and 19-31% Ce - Figure 1 As shown in Figure 1, the maximum energy product (BH) nax and coercive force iHc are approximately 26 %, and in the range of 20 to 30% cerium content good magnetic properties, in particular good maximum energy product (BH) nax and coercive force iHc, are obtained. (2) Composition of 26% Ce, 14% Fe, 2.5% Zr and 2 to 10% Cu - Figure 2 From Figure 2, good maximum energy product (BH) nax in the range of 3 to 9% copper content. It can be seen that the coercive force iHc is obtained. The graph of maximum energy product (BH) nax in Figure 2 shows that the maximum energy product (BH) n
It is noted that ax is at a maximum and there is a significant influence of the zirconium-containing phase. (3) Composition of 26% Ce, 7% Cu, 2.6% Zr and 6-35% Fe - Figure 3 Based on the trends of maximum energy product (BH) nax and coercive force iHc as seen in Figure 3, the present invention In this case, the iron content was set in the range of 10 to 30%. In addition, in Figure 3, the maximum values of the maximum energy product (BH) nax and coercive force iHc are obtained at high iron contents, where these values decrease in conventional precipitation hardening permanent magnets. is also attracting attention. (4) 26%Ce, 7.1%Cu, 14%Fe and 0.5~6%Zr
-Figure 4 Maximum energy product (BH) nax , residual magnetic flux density B r
The range of the present invention is a zirconium content of 1 to 5%, centering on about 3% zirconium at which the coercive force iHc becomes maximum. Example 2 Test materials having the compositions shown in Table 1 were prepared in the same manner as in Example 1. However, the sintering and heat treatment conditions were the same as in Example 1. The magnetic properties of the permanent magnet thus obtained are shown in Table 1.
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ãªç£æ°ç¹æ§ãåŸãã[Table] Sample materials 1 to 3 are examples of Ce-Zr type.
Maximum energy product (BH) nax and over 15.0MGOe
It shows a coercive force iHc of 4000Oe or more. Sample materials 4 to 7 are examples of the Ce-Zr (partially substituted) system, and test materials 8 to 10 are examples of the Ce (partially substituted with Sm)-Zr (partially substituted) system. These specimens 4 to 10 exhibit magnetic properties equal to or higher than those of specimens 1 to 3. Sample materials 11 to 14 show improvement in magnetic properties when the amount of Ce substituted for Sm is increased. Example 3 Raw metals were mixed to have a predetermined composition, and this mixed metal was melted, crushed, sintered, solutionized, and heat treated in the same manner as in Example 2 to obtain magnetic properties as shown in Table 2. Obtained.
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ããçµæã第ïŒè¡šã«ç€ºãã[Table] The test materials in Table 2 have some of the iron replaced with manganese, nickel, and chromium shown in the table, and exhibit good magnetic properties. Example 4 An energy dispersive X-ray spectrometer was attached to a scanning transmission electron microscope, and the composition was within the scope of the present invention.
The microstructures of Ce-Sm-Co-Fe precipitation-hardened permanent magnet specimens with different coercive forces iHc were observed, Zr-containing phases were identified, and their spacing was measured. The observation plane was the a-plane of the intermetallic compound crystal. The heat treatment conditions were the same as in Example 1, but the isothermal aging temperature was changed to 850°C.
The coercive force iHc was changed by changing the isothermal aging time from a minimum of 3 minutes to a maximum of 1000 minutes. The results are shown in Table 3.
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ããªãã[Table] From Table 3, the average spacing d of zirconium-containing phases
It can be seen that there is a relationship in which as the coercive force iHc becomes smaller, the coercive force iHc becomes higher. Therefore, in the present invention, the average spacing d of the zirconium-containing phase is set to 5000 Ã
or less, preferably 2000 Ã
or less, in order to obtain a sufficiently high coercive force. Example 5 When preparing a test material with the composition of the present invention (26% Ce, 7% Cu, 14% Fe, and 2.4% Zr) using the same procedure as in Example 1, the heat treatment conditions at each stage were changed. The coercive force iHc was measured. (1) Isothermal aging temperature (700, 750, 850, 900â) and time - Figure 5 From Figure 5, when the isothermal aging temperature is 700â, the coercive force iHc of the final treated specimen is low. ,
Even if the subsequent heat treatment is performed as described above, no zirconium-containing phase is produced. Next, when the isothermal aging temperature is 750°C or 850°C, two peaks occur in the coercive force. In the conventional isothermal aging method, the peak on the short time side was used as the isothermal aging treatment time. In the present invention, the longer peak is used as the isothermal aging treatment time, and in conjunction with other appropriate heat treatments, the zirconium-containing phase is present in the final product. (2) Heat treatment at 850â for 100 minutes followed by cooling to a temperature of 600, 650 or 700â at a cooling rate of 0.1 to 30 minutesâ/minute - Figure 6 As seen in Figure 6, isothermal aging treatment The cooling drop temperature and speed from the aging treatment temperature are each 600â
And 5â/min is the best, and 2~650â
Good coercive force even when cooled at a cooling rate of 10â/min
It can be seen that iHc can be obtained. (3) 0.1~ from 450, 500, 600 or 650â to 300â
Heat treatment with cooling at 30â/min - Figure 7 From the effect of heat treatment on the coercive force iHc shown in Figure 7, the cooling rate of 2â/min or less and the temperature range to which this cooling rate is applied are 500 to 650.
A good coercive force iHc can be obtained at â. Example 6 An example of a microstructure photograph (crystal a-plane) of a permanent magnet according to the present invention is shown in FIG. A large number of zirconium-containing phases exist perpendicularly to the c-axis direction, that is, parallel to the c-plane. FIG. 9 shows the results of energy dispersive X-ray spectroscopy measurements inside the cell structure between the zirconium-containing phases. The solid line in the figure is R(CoCu) 5 and the dotted line is R 2 (CoFeCu) 17 . As shown in FIG. 9, zirconium is not detected in areas where no zirconium-containing phase exists, and two types of crystals are present. As shown in Figure 10, from the part where the zirconium-containing phase exists, R 2 (CoFeCu) 17 phase (solid line) and R 2
(CoFeCuZr) 17 phases (dotted line) are detected (note that R
indicates a rare earth element). Therefore, it was found that Zr was contained together with Cu in the R 2 Co 17 phase.
Note that the R 2 (CoFeCu) 17 phase is detected separately from the R 2 (CoFeCuZr) 17 phase in X-ray spectroscopy, but
In Figure), both phases are not detected separately. Sm2 containing 1.5% Zr for comparison
(CoFeCu) A 17 -type magnet was subjected to isothermal aging treatment at 850°C for 10 minutes (conditions near the first peak as shown in Figure 5), and other heat treatments were performed within the above-mentioned condition range of the present invention. FIG. 11 shows the electron microscope structure of the treated sample material. In this structure, only the cell structure of the copper-containing phase exists, and no zirconium-containing phase is detected.
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Figures 1 to 4 show cerium, copper,
Graphs showing the magnetic properties when the iron and zirconium contents are changed. Figures 5 to 7 show the coercive force iHc when the conditions of isothermal aging treatment, cooling from isothermal aging, and aging treatment are changed, respectively. FIG. 8 is a scanning electron micrograph showing the metal structure of the permanent magnet of the present invention; FIGS. 9 and 10 are energy dispersion spectrograms of the inside of the cell structure of the permanent magnet and the zirconium-containing phase; FIG. 11 is an electron micrograph showing the metal structure of a conventional permanent magnet.
Claims (1)
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åšããããšãç¹åŸŽãšããæ°žä¹ ç£ç³ã[Claims] 1. 20 to 30% cerium by weight percentage, 3.
In a permanent magnet comprising an intermetallic compound containing 1 to 9% copper, 1 to 5% zirconium, and 10 to 30% iron, the balance being cobalt, the intermetallic compound mainly consisting of rare earth cobalt, the intermetallic compound A permanent magnet characterized in that zirconium-containing phases exist parallel to the c-plane of the crystal at an average spacing of 5000 Ã or less. 2 20 to 30% cerium by weight percentage, 3
or 9% copper, more than 1% and less than 5% hafnium, at least one metal from the group consisting of titanium, vanadium, niobium and tantalum, and zirconium (provided that zirconium is present in 1% or more and less than 5%), and In a permanent magnet comprising an intermetallic compound containing 10 to 30% iron, the balance being cobalt, and mainly consisting of rare earth cobalt, zirconium and at least one of the above-mentioned A permanent magnet characterized in that phases containing certain metals exist at an average distance of 5000 Ã or less. 3. In weight percentages, 20 to 30% cerium and samarium (with the exception that samarium is present at less than 80% (not including 0) of the total weight of cerium and samarium), 3 to 9% copper, 1 to 5% In a permanent magnet comprising an intermetallic compound containing zirconium and 10 to 30% iron, the balance being cobalt, the zirconium-containing phase is parallel to the c-plane of the crystal of the intermetallic compound. are present at an average distance of 5000 Ã or less. 4 By weight percentage, 20 to 30% cerium and samarium (however samarium is present at less than 80% (not including 0) of the total weight of cerium and samarium), 3 to 9% copper, more than 1%5 % or less of at least one metal from the group consisting of hafnium, titanium, vanadium, niobium, and tantalum and zirconium (however, zirconium is 1% or more and 5%
present), and containing 10 to 30% iron;
In a permanent magnet comprising an intermetallic compound mainly composed of rare earth cobalt, the balance being cobalt, the phases containing zirconium and the at least one metal are mutually parallel to the c-plane of the crystal of the intermetallic compound. A permanent magnet characterized by an average spacing of 5000 Ã or less. 5 cerium, 20 to 30% by weight, 3
9% copper, 1% to 5% zirconium,
and 10 to 30% of at least one metal from the group consisting of manganese, nickel, and chromium, and iron (but not more than 80% (excluding zero) of the total weight of iron and the at least one metal). In a permanent magnet comprising an intermetallic compound mainly composed of rare earth cobalt, the balance is cobalt, and the zirconium-containing phase is parallel to the c-plane of the intermetallic compound crystal, and the balance is cobalt. The interval is
A permanent magnet characterized by its existence at a thickness of 5000 Ã or less. 6 20 to 30% cerium by weight percentage, 3
or 9% copper, more than 1% and less than 5% hafnium, at least one metal of the first group consisting of titanium, vanadium, niobium and tantalum, and zirconium (provided that zirconium is present in 1% or more and less than 5%) , 10 to 30% manganese, nickel,
and at least one metal of the second group consisting of chromium and iron (however, 80% or less (not including 0) of the total weight of iron and the at least one metal is present) However, in a permanent magnet comprising an intermetallic compound mainly composed of rare earth cobalt, with the remainder being cobalt, a phase containing zirconium and the metal of the first group is parallel to the c-plane of the crystal of the intermetallic compound. Average spacing between each other is 5000
A permanent magnet characterized by being present at à or less. 7. In weight percentages, 20 to 30% cerium and samarium (with the exception that samarium is present at less than 80% (not including 0) of the total weight of cerium and samarium), 3 to 9% copper, 1 to 5% Zirconium, 10 to 30% of at least one metal from the group consisting of manganese, nickel and chromium, and iron (provided that the total weight of iron and at least one metal is
80% or less (excluding 0) of the at least one metal present), the balance being cobalt, and the permanent magnet comprising an intermetallic compound mainly composed of rare earth cobalt, the intermetallic compound A permanent magnet characterized in that zirconium-containing phases exist parallel to the c-plane of the crystal at an average spacing of 5000 Ã or less. 8 By weight percentage, 20 to 30% cerium and samarium (however samarium is present at less than 80% (not including 0) of the total weight of cerium and samarium), 3 to 9% copper, more than 1%5 % or less of at least one metal of the first group consisting of hafnium, titanium, vanadium, niobium, and tantalum and zirconium (however, zirconium is present in an amount of 1% or more and less than 5%), and 10 to 30% of manganese, nickel, and Contains at least one metal of the second group consisting of chromium and iron (however, 80% or less (not including 0) of the total weight of iron and the one metal is present), with the balance being is made of cobalt,
In a permanent magnet comprising an intermetallic compound mainly composed of rare earth cobalt, the phases containing zirconium and the first group metal are arranged parallel to the c-plane of the crystal of the intermetallic compound with an average spacing of 5000 Ã or less. Permanent magnet characterized by the presence of.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP56164826A JPS5866305A (en) | 1981-10-15 | 1981-10-15 | Permanent magnet |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP56164826A JPS5866305A (en) | 1981-10-15 | 1981-10-15 | Permanent magnet |
Publications (2)
Publication Number | Publication Date |
---|---|
JPS5866305A JPS5866305A (en) | 1983-04-20 |
JPH0252413B2 true JPH0252413B2 (en) | 1990-11-13 |
Family
ID=15800648
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP56164826A Granted JPS5866305A (en) | 1981-10-15 | 1981-10-15 | Permanent magnet |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPS5866305A (en) |
Families Citing this family (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH01225101A (en) * | 1988-03-04 | 1989-09-08 | Shin Etsu Chem Co Ltd | Rare earth permanent magnet |
JP5504233B2 (en) * | 2011-09-27 | 2014-05-28 | æ ªåŒäŒç€Ÿæ±è | PERMANENT MAGNET AND ITS MANUFACTURING METHOD, AND MOTOR AND GENERATOR USING THE SAME |
JP5710818B2 (en) * | 2014-03-14 | 2015-04-30 | æ ªåŒäŒç€Ÿæ±è | Permanent magnet, motor and generator using the same |
-
1981
- 1981-10-15 JP JP56164826A patent/JPS5866305A/en active Granted
Also Published As
Publication number | Publication date |
---|---|
JPS5866305A (en) | 1983-04-20 |
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