JPS63272009A - Manufacture of rare earth-fe-b magnet - Google Patents
Manufacture of rare earth-fe-b magnetInfo
- Publication number
- JPS63272009A JPS63272009A JP62104368A JP10436887A JPS63272009A JP S63272009 A JPS63272009 A JP S63272009A JP 62104368 A JP62104368 A JP 62104368A JP 10436887 A JP10436887 A JP 10436887A JP S63272009 A JPS63272009 A JP S63272009A
- Authority
- JP
- Japan
- Prior art keywords
- powder
- alloy powder
- magnetic
- rare earth
- hot pressing
- 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.)
- Pending
Links
- 238000004519 manufacturing process Methods 0.000 title claims description 15
- 239000000843 powder Substances 0.000 claims abstract description 40
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 32
- 239000000956 alloy Substances 0.000 claims abstract description 32
- 238000007731 hot pressing Methods 0.000 claims abstract description 28
- 229910001004 magnetic alloy Inorganic materials 0.000 claims abstract description 23
- 229910052751 metal Inorganic materials 0.000 claims abstract description 21
- 239000002184 metal Substances 0.000 claims abstract description 21
- 238000000034 method Methods 0.000 claims abstract description 12
- 229910052761 rare earth metal Inorganic materials 0.000 claims abstract description 10
- 229910052796 boron Inorganic materials 0.000 claims abstract description 6
- 229910052742 iron Inorganic materials 0.000 claims abstract description 4
- 238000003825 pressing Methods 0.000 claims description 5
- 239000006247 magnetic powder Substances 0.000 abstract description 23
- 230000007797 corrosion Effects 0.000 abstract description 10
- 238000005260 corrosion Methods 0.000 abstract description 10
- 230000004907 flux Effects 0.000 abstract description 9
- 229910052799 carbon Inorganic materials 0.000 abstract description 4
- 229910052684 Cerium Inorganic materials 0.000 abstract description 3
- 229910052779 Neodymium Inorganic materials 0.000 abstract description 3
- 229910052777 Praseodymium Inorganic materials 0.000 abstract description 3
- 239000000203 mixture Substances 0.000 abstract description 2
- 230000004927 fusion Effects 0.000 abstract 3
- 238000010298 pulverizing process Methods 0.000 abstract 1
- 238000009987 spinning Methods 0.000 abstract 1
- 230000000694 effects Effects 0.000 description 6
- 230000000052 comparative effect Effects 0.000 description 5
- 238000002844 melting Methods 0.000 description 5
- 230000008018 melting Effects 0.000 description 5
- 229910000679 solder Inorganic materials 0.000 description 5
- 230000007423 decrease Effects 0.000 description 4
- 239000000155 melt Substances 0.000 description 3
- 150000002739 metals Chemical class 0.000 description 3
- 239000011812 mixed powder Substances 0.000 description 3
- 238000000465 moulding Methods 0.000 description 3
- 241000269821 Scombridae Species 0.000 description 2
- 239000000654 additive Substances 0.000 description 2
- 230000000996 additive effect Effects 0.000 description 2
- 230000008901 benefit Effects 0.000 description 2
- 239000003822 epoxy resin Substances 0.000 description 2
- 230000006698 induction Effects 0.000 description 2
- 239000007791 liquid phase Substances 0.000 description 2
- 230000001050 lubricating effect Effects 0.000 description 2
- 235000020640 mackerel Nutrition 0.000 description 2
- 238000002074 melt spinning Methods 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 229910052698 phosphorus Inorganic materials 0.000 description 2
- 229920000647 polyepoxide Polymers 0.000 description 2
- 150000002910 rare earth metals Chemical class 0.000 description 2
- 229910017944 Ag—Cu Inorganic materials 0.000 description 1
- 229910000925 Cd alloy Inorganic materials 0.000 description 1
- 229910002482 Cu–Ni Inorganic materials 0.000 description 1
- 229910052692 Dysprosium Inorganic materials 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 229910002056 binary alloy Inorganic materials 0.000 description 1
- 229910052792 caesium Inorganic materials 0.000 description 1
- 230000008094 contradictory effect Effects 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 229910052733 gallium Inorganic materials 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 229910052738 indium Inorganic materials 0.000 description 1
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 1
- 229910052745 lead Inorganic materials 0.000 description 1
- 229910052744 lithium Inorganic materials 0.000 description 1
- 229910001172 neodymium magnet Inorganic materials 0.000 description 1
- 239000004033 plastic Substances 0.000 description 1
- 229910052700 potassium Inorganic materials 0.000 description 1
- 229910002059 quaternary alloy Inorganic materials 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 229910052711 selenium Inorganic materials 0.000 description 1
- 229910052708 sodium Inorganic materials 0.000 description 1
- 229910052950 sphalerite Inorganic materials 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 229910002058 ternary alloy Inorganic materials 0.000 description 1
- 229910052718 tin Inorganic materials 0.000 description 1
- 229910052727 yttrium Inorganic materials 0.000 description 1
- 229910052984 zinc sulfide Inorganic materials 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
- H01F1/057—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B
- H01F1/0571—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes
- H01F1/0575—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes pressed, sintered or bonded together
- H01F1/0576—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes pressed, sintered or bonded together pressed, e.g. hot working
Landscapes
- Chemical & Material Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Inorganic Chemistry (AREA)
- Engineering & Computer Science (AREA)
- Power Engineering (AREA)
- Powder Metallurgy (AREA)
- Hard Magnetic Materials (AREA)
Abstract
Description
【発明の詳細な説明】 （産業上の利用分野） 本発明は希土類−Ｆｅ−Ｂ系磁石の製造方法に関する。[Detailed description of the invention] (Industrial application field) The present invention relates to a method for manufacturing a rare earth-Fe-B magnet.
（従来技術及び発明が解決しようとする問題点）従来、
Ｎｄ−Ｆｅ−Ｂ系磁石を始めとする希土類−Ｆｅ−Ｂ系
磁石を製造する方法の１つとして、これらの各元素を主
成分とする磁性合金粉末を加圧焼結即ちホットプレスし
て所望の形状の磁石とする方法が知られている。このホ
ットプレスによる製造方法は、例えば、前記磁性合金粉
末にエポキシ樹脂等を混合・成形する方法に比べて、高
密度即ち高エネルギー積の磁石が得られるという利点を
有している。(Prior art and problems to be solved by the invention) Conventionally,
One method for manufacturing rare earth-Fe-B magnets, including Nd-Fe-B magnets, is to pressure-sinter, or hot-press, magnetic alloy powders containing these elements as the main components. A method of making a magnet with the shape of is known. This manufacturing method using hot pressing has an advantage over, for example, the method of mixing and molding the magnetic alloy powder with an epoxy resin or the like in that a magnet with a high density, that is, a high energy product can be obtained.
ところが、上記ホットプレスを適用した製造方法におい
ては、磁性粉末の密度を充分に高め、エネルギー積を向
上させるためには、ホントプレス温度を６７０℃以上と
する必要があるが、一方、残留磁束密度及び保磁力を高
めるためには６７０℃以下の温度とすることが好ましい
、従って、このような二律背反する条件を共に満足する
ホットプレス温度の設定が困難であるという問題があっ
た。However, in the manufacturing method using hot pressing, in order to sufficiently increase the density of magnetic powder and improve the energy product, it is necessary to set the real pressing temperature to 670°C or higher, but on the other hand, the residual magnetic flux density In order to increase the coercive force, it is preferable to set the temperature to 670° C. or lower.Therefore, there has been a problem in that it is difficult to set a hot press temperature that satisfies both of these contradictory conditions.
更に、上記希土類−Ｆｅ−Ｂ系磁石は一般に耐蝕性が低
く、使用時に鯖が生じるため、表面をコ−ティングする
ことが必要であった。Furthermore, the above-mentioned rare earth-Fe-B magnets generally have low corrosion resistance and scorch occurs during use, so it is necessary to coat the surface.
本発明は上記従来の問題点に鑑みてなされたもので、ホ
ットプレス法を適用して希土類−Ｆｅ−Ｂ系磁石を製造
する方法において、磁性粉末密度を高めると共に、残留
磁束密度、保磁力及びエネルギー積などの磁気特性を高
めることが可能であり、しかも、耐蝕性を向上しうる希
土類−Ｆｅ−Ｂ系磁石の製造方法を提供することを目的
とする。The present invention has been made in view of the above-mentioned conventional problems, and is a method for manufacturing rare earth-Fe-B magnets by applying a hot press method, in which the density of magnetic powder is increased, the residual magnetic flux density, coercive force and It is an object of the present invention to provide a method for manufacturing a rare earth-Fe-B magnet that can improve magnetic properties such as energy product and corrosion resistance.
（問題点を解決するための手段及び作用）本発明は、先
ずホットプレス温度を６７０℃以下として高い保磁力を
確保すると共に、磁性粉末にホットプレス温度で液相と
なる金属もしくは合金粉末を添加混合することにより、
残留磁束密度を向上させると共に、密度を高めてエネル
ギー積を向上させ、更に、耐蝕性の向上を実現したもの
である。(Means and effects for solving the problems) The present invention first secures a high coercive force by setting the hot press temperature to 670°C or less, and also adds metal or alloy powder that becomes a liquid phase at the hot press temperature to the magnetic powder. By mixing,
In addition to improving the residual magnetic flux density, the density is increased to improve the energy product, and furthermore, corrosion resistance is improved.
即ち、本発明は少なくとも１種の希土類元素、Ｐｅ及び
Ｂを主成分とする磁性合金粉末をホットプレスして希土
１ｉ−Ｐａ−Ｂ系磁石を製造する方法において、前記ホ
ットプレスを６７０℃以下の温度で行うと共に、このホ
ットプレス時に溶融状態にあるような金属もしくは合金
粉末を前記磁性合金粉末に添加混合したのち、前記ホッ
トプレスを行うこととしたものである。That is, the present invention provides a method for producing a rare earth 1i-Pa-B magnet by hot pressing a magnetic alloy powder containing at least one rare earth element, Pe and B as main components, in which the hot pressing is performed at 670°C or lower. At the same time, the hot pressing is carried out after adding and mixing a metal or alloy powder which is in a molten state at the time of the hot pressing to the magnetic alloy powder.
本発明の希土類−Ｆｅ−Ｂ系磁石の製造方法において、
先ず、使用する磁性合金粉末としては、少なくとも１種
の希土類元素、Ｆｅ及びＢ主成分とするものである。希
土類元素としては、特に限定されるものではないが、特
に、Ｎｄ、Ｐｒ、Ｃｅ。In the method for manufacturing a rare earth-Fe-B magnet of the present invention,
First, the magnetic alloy powder used is one containing at least one rare earth element, Fe, and B as main components. Rare earth elements include, but are not particularly limited to, Nd, Pr, and Ce.
［）ｙ、Ｙ、Ｓｍ５Ｈａ、Ｅｒが好適であり、Ｄｙのよ
うな重希土類元素を添加すると、保磁力を向上させるう
えで効果的である。又、Ｂの一部をＳｔ。[)y, Y, Sm5Ha, and Er are preferable, and adding a heavy rare earth element such as Dy is effective in improving the coercive force. Also, a part of B is St.
Ｎ、Ｃ，Ｐ等で置換することもできる。又、Ｆｅの一部
をＣｏで置換すると、キュリ一温度を上昇させるのに効
果的である。Substitution with N, C, P, etc. is also possible. Furthermore, replacing a portion of Fe with Co is effective in increasing the Curie temperature.
次いで、かかる磁性合金粉末に添加混合する金属もしく
は合金としては、６７０℃以下のホットプレス時に溶融
状態にあるものであれば、特に限定されるものではない
、一般的には、大気圧中での融点が６７０℃以下の金属
もしくは合金が使用されるが、ホットプレス時には温度
のみならず圧力も印加されるので、実際には、大気圧中
の融点がホットプレス温度よりも多少高めのものも使用
できる場合がある。以下に、かかる金属もしくは合金の
具体例を示すと、Ｌ ｉ、Ｎａ％Ｍｇ、Ａｊ’。Next, the metal or alloy to be added to and mixed with the magnetic alloy powder is not particularly limited as long as it is in a molten state when hot pressed at 670°C or lower. A metal or alloy with a melting point of 670°C or less is used, but since not only temperature but also pressure is applied during hot pressing, in reality, metals or alloys with a melting point at atmospheric pressure slightly higher than the hot pressing temperature are also used. There are cases where it is possible. Specific examples of such metals or alloys are shown below: Li, Na%Mg, Aj'.
Ｐ、 Ｓ、 Ｋ、 ＺｎＳ Ｇａ、 Ｓｅ、
Ｒｈ、 Ｃｄｓ Ｉｎ、Ｓｎ、５ｂＳＴｏ、Ｌ
Ｃｓ、ＴＩ、Ｐｂ、Ｂ１％ＰＯ１Ａｔ、Ｆｒ等の金属、
５ｎ−Ｐｂ系、Ｃｕ−３ｎ系、Ｃｒ−３ｂ系、Ｃｏ−３
ｎ系、Ａｊ−８ｉ系、Ａｊ−Ｚｎ系合金等の２元系合金
、５ｎ−３ｂ−Ｃｕ系、５ｎ−３ｂ−Ｐｂ系、５ｎ−Ｃ
ｕ−Ｚｎ系、Ａｌ−３ｎ−Ｃｕ系、Ｃｄ−Ｎ１−’ｌｎ
系、Ｃｄ−Ａｇ−Ｃｕ系合金等の３元系合金、５ｎ−３
ｂ−Ｐｂ−Ｃｕ系、Ａｎ−３ｎ−Ｃｕ−Ｎｉ系、Ｂ１−
Ｐｂ−３ｎ−Ｃｄ系合金等の４元系合金などをあげるこ
とができる。P, S, K, ZnS Ga, Se,
Rh, Cds In, Sn, 5bSTo, L
Metals such as Cs, TI, Pb, B1%PO1At, Fr,
5n-Pb system, Cu-3n system, Cr-3b system, Co-3
Binary alloys such as n series, Aj-8i series, Aj-Zn series alloys, 5n-3b-Cu series, 5n-3b-Pb series, 5n-C
u-Zn series, Al-3n-Cu series, Cd-N1-'ln
ternary alloys such as Cd-Ag-Cu alloys, 5n-3
b-Pb-Cu system, An-3n-Cu-Ni system, B1-
Examples include quaternary alloys such as Pb-3n-Cd alloys.
以下に本発明の製造工程を順次説明する。先ず、前記磁
性粉末に上記の金属もしくは合金粉末を添加混合する。The manufacturing steps of the present invention will be sequentially explained below. First, the above-mentioned metal or alloy powder is added and mixed with the above-mentioned magnetic powder.
この金属もしくは合金粉末の添加量は特に限定されるも
のではなく、又、この金属もしくは合金の種類、或いは
、磁性合金粉末の種類によっても異なるが、一般に、磁
性合金粉末に対して、１〜５０重量％に設定することが
望ましい。The amount of the metal or alloy powder to be added is not particularly limited and varies depending on the type of metal or alloy or the type of magnetic alloy powder, but generally it is 1 to 50% of the magnetic alloy powder. It is desirable to set it to % by weight.
この添加量が１重量％未満であると、充分な添加効果が
得られず、磁性粉末成形体の密度を向上することができ
ない場合があり、５０重量％を超えると、単位体積当た
りの磁性粉末の量が減少して充分な磁気特性が得られな
い場合がある。If the amount added is less than 1% by weight, a sufficient addition effect may not be obtained and the density of the magnetic powder compact may not be improved. If it exceeds 50% by weight, the amount of magnetic powder per unit volume may not be improved. There are cases where sufficient magnetic properties cannot be obtained due to a decrease in the amount of .
次いで、上記の混合粉末をホットプレスして目的とする
磁石を製造する。この時の温度は、６７０℃以下で、且
つ、上記した添加金属もしくは合金を完全に溶融しうろ
温度に設定する必要がある。Next, the above mixed powder is hot pressed to produce the intended magnet. The temperature at this time must be set at 670° C. or lower and at a temperature at which the above-mentioned additive metal or alloy is completely melted.
ホットプレス温度が６７０℃を超えると、前述したよう
に、磁性粉末の磁気特性が大幅に低下してしまう、又、
ホットプレス温度が、上記添加金属もしくは合金粉末を
溶融する温度より低い場合は、当該金属もしくは合金粉
末の添加効果が発揮されず、磁性粉末成形体の密度を高
めることができないと同時に、耐蝕性の向上も期待でき
ないという不都合が生じる。If the hot press temperature exceeds 670°C, as mentioned above, the magnetic properties of the magnetic powder will decrease significantly;
If the hot pressing temperature is lower than the temperature at which the above-mentioned additive metal or alloy powder is melted, the effect of adding the metal or alloy powder will not be exhibited, and the density of the magnetic powder compact will not be increased, and at the same time, the corrosion resistance will deteriorate. This causes the inconvenience that no improvement can be expected.
このように、磁性粉末に、６７０℃以下のホットプレス
時に溶融する金属もしくは合金粉末を添加することによ
って前記磁性粉末成形体の密度が向上する原因は、溶融
金属もしくは合金が潤滑作用を有しており、この潤滑作
用によって磁性粉末のホットプレス時の空孔の発生が防
止されるためであると考えられる。As described above, the reason why the density of the magnetic powder compact is improved by adding a metal or alloy powder that melts during hot pressing at 670°C or less to the magnetic powder is that the molten metal or alloy has a lubricating effect. This is thought to be because this lubricating action prevents the generation of voids during hot pressing of the magnetic powder.
更に、ホットプレス時に金属もしくは合金粉末が熔融し
て磁性粉末を云わばコーティングするため、当該磁性粉
末の耐蝕性が向上するという利点がある。Furthermore, since the metal or alloy powder melts during hot pressing and coats the magnetic powder, there is an advantage that the corrosion resistance of the magnetic powder is improved.
（実施例）
１１ １〜４、
重量％で、Ｎｄ：２５％、Ｐｒ：３％、Ｃｅ：１％、Ｂ
：０．５％、Ｓｉ：０．２％、Ｃｏ：３％、及び、残部
Ｆｅよりなる組成の合金を誘導炉にて製造した。この合
金を溶融スピニング法によりリボン状薄帯としたのち、
−６０メツシユに粉砕して磁性合金粉末を得た０次いで
、この磁性合金粉末にＡｊ（融点：６６０℃）粉末を第
１表に示した各添加量（重量％）で添加混合し、しかる
のち、この混合粉末を第１表に示した条件でホットプレ
スすることにより、希±１９−Ｆｅ−Ｂ系磁石を製造し
た。(Example) 11 1 to 4, in weight%, Nd: 25%, Pr: 3%, Ce: 1%, B
An alloy having a composition of: 0.5%, Si: 0.2%, Co: 3%, and the balance Fe was produced in an induction furnace. After making this alloy into a ribbon-like thin strip by melt spinning method,
Aj (melting point: 660°C) powder was added to the magnetic alloy powder in the amount (wt%) shown in Table 1 and then mixed. By hot pressing this mixed powder under the conditions shown in Table 1, rare ±19-Fe-B magnets were manufactured.
上記により得られた各磁石につき、その磁気特性、密度
を夫々測定して第１表中に示した。尚、表に示したＢ−
Ｈ磁気特性において、上段の数値はプレス方向と平行な
方向の値、下段の数値はプレス方向と直角な方向の値を
夫々示しである。更に、実際の残留磁束密度の評価は、
プレス方向と平行方向の残留磁束密度（Ｂ ｒｌｌ ）
と直角方向の残留磁束密度（Ｂｒ上）との和に、体積％
による補正係数を乗じたものを算出することにより行っ
た。即ち、実際の残留磁束密度Ｂｒ□。１．。は、次式
（ｉ）：’
Ｂｒ１ＬａＬａｌｌ −１／ Ｆ （Ｂ ｒ７７ ＋
Ｂ ｒｌ ） ・＝（１１であり、Ｆは、次式（２）
：
％式％
（但し、式（２）中、ρは測定された磁性粉末成形体の
密度、ρ、は磁性粉末の真密度、Ｘは磁性粉末の重量％
を夫々示し、結果として、Ｆは磁性粉末の体積％を表し
ている。）である。The magnetic properties and density of each of the magnets obtained above were measured and shown in Table 1. In addition, B- shown in the table
In the H magnetic properties, the numerical values in the upper row indicate values in the direction parallel to the pressing direction, and the numerical values in the lower row indicate the values in the direction perpendicular to the pressing direction. Furthermore, the actual evaluation of residual magnetic flux density is
Residual magnetic flux density in the direction parallel to the pressing direction (B rll )
and the residual magnetic flux density in the perpendicular direction (on Br), volume %
This was done by calculating the value multiplied by a correction coefficient. That is, the actual residual magnetic flux density Br□. 1. . is the following formula (i):' Br1LaLall -1/F (Br77 +
B rl ) ・= (11, and F is the following formula (2)
: % formula % (However, in formula (2), ρ is the measured density of the magnetic powder compact, ρ is the true density of the magnetic powder, and X is the weight % of the magnetic powder.
As a result, F represents the volume percent of the magnetic powder. ).
尚、第１表中には、参考例として、上記と同様の磁性合
金粉末を真空中６００℃で１時間熱処理したのち、エポ
キシ樹脂を２１ｉ量％混合し、成形圧カフ ｔｏｎｆ／
−でプレス成形してなる所謂プラスチック磁石を製造し
て、その磁気特性及び密度を併せて示した。In Table 1, as a reference example, the same magnetic alloy powder as above was heat-treated at 600°C in vacuum for 1 hour, and then 21i% of epoxy resin was mixed therein, and the molding pressure cuff tonf/
- A so-called plastic magnet was produced by press molding, and its magnetic properties and density were also shown.
２、 ５〜７
重量％で、Ｎｄ：２Ｔ％、Ｄｙ：１重量％、Ｂ：０．４
％、Ｎ１．０１％、ｓｔ：ｏ、ｔ％、Ｃ：０．１％、及
び、残部Ｆｅよりなる組成の磁性合金を誘導炉にて製造
した。この合金を溶融スピニング法によりリボン状薄帯
としたのち、−６０メツシユに粉砕して磁性合金粉末を
得た０次いで、この磁性合金粉末にはんだ合金（６３重
量％５ｎ−３７重量％ｐｂ、融点：１８３℃）粉末を第
２表に示した各添加量（重量％）で添加混合し、しかる
のち、この混合粉末を第２表に示した条件でホットプレ
スすることにより、希土類−Ｆｅ−Ｂ系磁石を製造した
。2, 5-7% by weight, Nd: 2T%, Dy: 1% by weight, B: 0.4
%, N 1.01%, st: o, t%, C: 0.1%, and the balance was produced in an induction furnace. This alloy was made into a ribbon-like thin strip by a melt spinning method, and then ground into a -60 mesh to obtain a magnetic alloy powder.Next, this magnetic alloy powder was mixed with a solder alloy (63% by weight 5N-37% by weight PB, melting point : 183℃) powder in the amounts (wt%) shown in Table 2, and then hot-pressed this mixed powder under the conditions shown in Table 2 to form rare earth -Fe-B. A system magnet was manufactured.
このようにして得られた各磁石について、上記と同様そ
の磁気特性及び密度を測定し、第２表中に示した。更に
、これらの磁石の耐蝕性を調べるために、各磁石を温度
５０℃、相対湿度９８％の雰囲気中に９６時間保持する
耐蝕試験を行い、磁石の全面積に対する鯖の発生面積の
比を算出して第２表中に併記した。The magnetic properties and density of each magnet thus obtained were measured in the same manner as above, and are shown in Table 2. Furthermore, in order to examine the corrosion resistance of these magnets, we conducted a corrosion resistance test in which each magnet was held in an atmosphere with a temperature of 50°C and a relative humidity of 98% for 96 hours, and the ratio of the area where mackerel was generated to the total area of the magnet was calculated. and are also listed in Table 2.
（以下余白）
第１表において、ホットプレス温度が６７０℃を超える
場合はＡＪを添加するしないにかかわらず、保磁力が低
下してしまう（比較例２．４）。(The following is a blank space) In Table 1, when the hot press temperature exceeds 670°C, the coercive force decreases regardless of whether AJ is added or not (Comparative Example 2.4).
そして、ホットプレス温度が６７０℃以下の場合、Ａｎ
を添加し、且つＡＩの融点６６０℃以上の温度の場合は
磁性粉末成形体の密度も高く、磁気特性も全て向上する
（実施例１）が、ＡＮを添加しない場合は磁性粉末成形
体の密度が小さく （比較例３） 、Ａｊ！を添加して
もＡＩが溶融しないような温度の場合は、磁性粉末成形
体の密度は極めて小さくなりエネルギー積が低下してし
まう（比較例１）ことが１ｉｉｉ！された。And when the hot press temperature is 670°C or less, An
When AN is added and the temperature is higher than the melting point of AI, 660°C, the density of the magnetic powder compact is high and all magnetic properties are improved (Example 1), but when AN is not added, the density of the magnetic powder compact is high. is small (Comparative Example 3), Aj! If the temperature is such that AI does not melt even if it is added, the density of the magnetic powder compact becomes extremely small and the energy product decreases (Comparative Example 1). It was done.
又、第２表において、磁気特性と磁性粉末成形体の密度
については、上記第１表と同様の結果が得られた。更に
、はんだ合金を添加していないものは、鯖の発生面積が
極めて大きく （比較例６．７）、又、はんだ合金を添
加してもこれが溶融しないような温度でホットプレスし
たものは、やはり鯖の発生面積が大きく１．添加効果が
殆ど発現していない（比較例５）が、はんだ合金を添加
し且つはんだ合金が溶融する温度でホットプレスしたも
のは、錆の発生面積が激減し、耐蝕性が著しく向上して
いることが明らかとなつた（実施例２）。Furthermore, in Table 2, the same results as in Table 1 above were obtained regarding the magnetic properties and the density of the magnetic powder compacts. Furthermore, the area where solder alloy is not added is extremely large (Comparative Example 6.7), and the product that is hot-pressed at a temperature that does not melt even if solder alloy is added is still 1. The area where mackerel occurs is large. Although almost no effect of the addition was observed (Comparative Example 5), the product to which solder alloy was added and hot-pressed at a temperature where the solder alloy melted had a drastic reduction in the area where rust occurred and significantly improved corrosion resistance. This became clear (Example 2).
（発明の効果ン
以上説明したように本発明によれば、少なくとも１種の
希土類元素、Ｆｅ及びＢを主成分とする磁性合金粉末を
ホットプレスして希土類−Ｆｅ−Ｂ系磁石を製造する方
法において、前記ホントプレスを６７０℃以下の温度で
行うと共に、このホットプレス時に溶融状態にあるよう
な金属もしくは合金粉末を前記磁性合金粉末に添加混合
したのち、前記ホットプレスを行うこととしたので、比
較的低温におけるホットプレスにより磁気特性特に保磁
力を確保すると共に、ホットプレス時に溶融して液相を
形成する金属もしくは合金の作用により磁性粉末成形体
の密度を高めて、残留磁束密度及びエネルギー積を向上
させることができる。更に、得られた磁石の耐蝕性を向
上させる効果も有する。(Effects of the Invention) As explained above, according to the present invention, a method for producing a rare earth-Fe-B magnet by hot pressing a magnetic alloy powder containing at least one rare earth element, Fe and B as main components. In this case, the hot pressing is performed at a temperature of 670° C. or lower, and after adding and mixing a metal or alloy powder that is in a molten state at the time of the hot pressing to the magnetic alloy powder, Hot pressing at a relatively low temperature ensures magnetic properties, especially coercive force, and the density of the magnetic powder compact is increased by the action of the metal or alloy that melts during hot pressing to form a liquid phase, resulting in improved residual magnetic flux density and energy product. Further, it has the effect of improving the corrosion resistance of the obtained magnet.
Claims (2)
分とする磁性合金粉末をホットプレスして希土類−Ｆｅ
−Ｂ系磁石を製造する方法において、前記ホットプレス
を６７０℃以下の温度で行うと共に、このホットプレス
時に溶融状態にあるような金属もしくは合金粉末を前記
磁性合金粉末に添加混合したのち、前記ホットプレスを
行うことを特徴とする希土類−Ｆｅ−Ｂ系磁石の製造方
法。(1) Hot pressing magnetic alloy powder containing at least one rare earth element, Fe and B as main components to produce rare earth-Fe
- In the method of manufacturing a B-based magnet, the hot pressing is performed at a temperature of 670°C or lower, and after adding and mixing a metal or alloy powder that is in a molten state at the time of the hot pressing to the magnetic alloy powder, A method for manufacturing a rare earth-Fe-B magnet, which comprises pressing.
に対して１〜５０重量％添加混合することを特徴とする
特許請求の範囲第１項記載の希土類−Ｆｅ−Ｂ系磁石の
製造方法。(2) The method for manufacturing a rare earth-Fe-B magnet according to claim 1, characterized in that the metal or alloy powder is added and mixed in an amount of 1 to 50% by weight with respect to the magnetic alloy powder.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62104368A JPS63272009A (en) | 1987-04-30 | 1987-04-30 | Manufacture of rare earth-fe-b magnet |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62104368A JPS63272009A (en) | 1987-04-30 | 1987-04-30 | Manufacture of rare earth-fe-b magnet |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS63272009A true JPS63272009A (en) | 1988-11-09 |
Family
ID=14378869
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP62104368A Pending JPS63272009A (en) | 1987-04-30 | 1987-04-30 | Manufacture of rare earth-fe-b magnet |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS63272009A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0434113A2 (en) * | 1989-12-19 | 1991-06-26 | General Motors Corporation | Alloying low-level additives into hot-worked Nd-Fe-B magnets |
| WO1997017709A1 (en) * | 1995-11-10 | 1997-05-15 | Magnetfabrik Schramberg Gmbh & Co. | MAGNETIC MATERIAL AND PERMANENT MAGNET OF THE NdFeB TYPE |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6386502A (en) * | 1986-09-30 | 1988-04-16 | Tokin Corp | Rare earth magnet and manufacture thereof |
-
1987
- 1987-04-30 JP JP62104368A patent/JPS63272009A/en active Pending
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6386502A (en) * | 1986-09-30 | 1988-04-16 | Tokin Corp | Rare earth magnet and manufacture thereof |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0434113A2 (en) * | 1989-12-19 | 1991-06-26 | General Motors Corporation | Alloying low-level additives into hot-worked Nd-Fe-B magnets |
| WO1997017709A1 (en) * | 1995-11-10 | 1997-05-15 | Magnetfabrik Schramberg Gmbh & Co. | MAGNETIC MATERIAL AND PERMANENT MAGNET OF THE NdFeB TYPE |
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