JPS63169357A - Magnetic alloy - Google Patents
Magnetic alloyInfo
- Publication number
- JPS63169357A JPS63169357A JP61315824A JP31582486A JPS63169357A JP S63169357 A JPS63169357 A JP S63169357A JP 61315824 A JP61315824 A JP 61315824A JP 31582486 A JP31582486 A JP 31582486A JP S63169357 A JPS63169357 A JP S63169357A
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- coercive force
- content
- rare earth
- composition
- 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
- 229910001004 magnetic alloy Inorganic materials 0.000 title claims abstract description 5
- 229910052761 rare earth metal Inorganic materials 0.000 claims abstract description 20
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 5
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 4
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 3
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 3
- 229910052802 copper Inorganic materials 0.000 claims abstract description 3
- 229910052735 hafnium Inorganic materials 0.000 claims abstract description 3
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 3
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 3
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 3
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 3
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 3
- 229910052782 aluminium Inorganic materials 0.000 claims abstract 3
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract 2
- 229910052715 tantalum Inorganic materials 0.000 claims abstract 2
- 229910052721 tungsten Inorganic materials 0.000 claims abstract 2
- 230000005291 magnetic effect Effects 0.000 abstract description 24
- 239000000203 mixture Substances 0.000 abstract description 22
- 229910052742 iron Inorganic materials 0.000 abstract description 11
- 229910045601 alloy Inorganic materials 0.000 abstract description 8
- 239000000956 alloy Substances 0.000 abstract description 8
- 230000004907 flux Effects 0.000 abstract description 8
- 229910052796 boron Inorganic materials 0.000 abstract description 7
- 229910052709 silver Inorganic materials 0.000 abstract 1
- 229910000640 Fe alloy Inorganic materials 0.000 description 23
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 19
- 238000000034 method Methods 0.000 description 10
- 230000007423 decrease Effects 0.000 description 8
- 150000001875 compounds Chemical class 0.000 description 4
- 239000007788 liquid Substances 0.000 description 4
- 238000010791 quenching Methods 0.000 description 4
- 230000000171 quenching effect Effects 0.000 description 4
- 229910017052 cobalt Inorganic materials 0.000 description 3
- 239000010941 cobalt Substances 0.000 description 3
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 238000002844 melting Methods 0.000 description 3
- 230000008018 melting Effects 0.000 description 3
- 229910052779 Neodymium Inorganic materials 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 238000006467 substitution reaction Methods 0.000 description 2
- -1 R-13 to 17% Chemical class 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- RKTYLMNFRDHKIL-UHFFFAOYSA-N copper;5,10,15,20-tetraphenylporphyrin-22,24-diide Chemical group [Cu+2].C1=CC(C(=C2C=CC([N-]2)=C(C=2C=CC=CC=2)C=2C=CC(N=2)=C(C=2C=CC=CC=2)C2=CC=C3[N-]2)C=2C=CC=CC=2)=NC1=C3C1=CC=CC=C1 RKTYLMNFRDHKIL-UHFFFAOYSA-N 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000001747 exhibiting effect Effects 0.000 description 1
- 230000005294 ferromagnetic effect Effects 0.000 description 1
- 238000007731 hot pressing Methods 0.000 description 1
- 239000012770 industrial material Substances 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000000843 powder Substances 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 239000011347 resin Substances 0.000 description 1
- 229920005989 resin Polymers 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 238000005245 sintering Methods 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 235000014347 soups Nutrition 0.000 description 1
- 229910000859 α-Fe 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
Landscapes
- Chemical & Material Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Inorganic Chemistry (AREA)
- Engineering & Computer Science (AREA)
- Power Engineering (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−鉄一ホウ素系永久磁石合金（以下、
Ｒ−Ｂ−Ｆｅ合金という）に関するものであり、さらに
詳しく述べるならば、新規な組織となるように組成を設
定して、磁石特性を改良したＲ−Ｂ−Ｆｅ合金に関する
ものである。[Detailed Description of the Invention] [Industrial Application Field] The present invention relates to a rare earth-iron-boron permanent magnet alloy (hereinafter referred to as
More specifically, it relates to an R-B-Fe alloy whose composition has been set to have a new structure and whose magnetic properties have been improved.
Ｒ−Ｂ −Ｆｅ合金永久磁石は、高価なコバルト等を必
須成分とせずにまた安価な工業材料である鉄を多量に用
いることによって、優れた磁石特性を実現する。これま
で、より一層の磁石特性の向上を図り、より安価な元素
を使用しつつ良好な磁石特性の達成し、あるいは加γ性
を向上する等の方法によって、従来の一般的永久磁石で
ある希土類コバルト永久磁石、フェライト磁石に代替し
、これらの磁石と競合できるＲ −Ｂ −Ｆｅ合金永久
磁石を提供するための研究が活発になされている。The R-B-Fe alloy permanent magnet achieves excellent magnetic properties by using a large amount of iron, which is an inexpensive industrial material, without using expensive cobalt as an essential component. Until now, efforts have been made to further improve the magnetic properties of conventional permanent magnets, such as achieving good magnetic properties while using cheaper elements, or improving gamma properties. Research is being actively conducted to provide an R-B-Fe alloy permanent magnet that can replace cobalt permanent magnets and ferrite magnets and can compete with these magnets.
Ｒ−Ｂ−Ｆｅ合金を磁気異方性焼結体とすることを提案
をする特公昭６１−３４２４２号公報の組成は、希土類
元素Ｒ（Ｎｄ、ＰｒＪ）１＋、Ｈｏ、Ｔｂ） ＝ ８〜
３０％、Ｂ＝２〜２８％、残部Ｆｅからなるものが特許
請求の範囲に記載されており、また実施例に示された組
成によると、希土類元素Ｒ＝１３〜１７％、Ｂ＝５〜８
％の範囲で特に優れた磁石特性が得られている。The composition of Japanese Patent Publication No. 61-34242, which proposes making an R-B-Fe alloy into a magnetically anisotropic sintered body, is as follows: rare earth elements R(Nd, PrJ)1+, Ho, Tb) = 8~
30%, B=2-28%, balance Fe is described in the claims, and according to the composition shown in the example, rare earth element R=13-17%, B=5-5 8
Particularly excellent magnetic properties were obtained within the range of %.
また、Ｒ−Ｂ−Ｆｅ合金に液体急冷法により高い保磁力
ｉＨｃとエネルギ積を具備させることを提案する特開昭
６０−９８５２号の組成は、希土類元素Ｒ（Ｎｄ、 Ｐ
ｒ） ＝ １０％以上、Ｂ＝０．５〜１０％、残部Ｆｅ
からなるものが特許請求の範囲に記載されている。Furthermore, the composition of JP-A-60-9852, which proposes to provide R-B-Fe alloy with high coercive force iHc and energy product by liquid quenching method, contains rare earth elements R (Nd, P
r) = 10% or more, B = 0.5 to 10%, balance Fe
What is described in the claims is:
従来Ｒ−Ｂ −Ｆｅ合金の優れた磁石特性はＮｄｚＦｅ
ｚＢ相化合物によるものと説明されており、そのため磁
石特性を改良するための多くの提案はこの化合物に該当
する組成の近傍、すなわち、Ｒ−１３〜１７％、Ｂ＝５
〜８％の範囲の合金の実験に基づいている。The excellent magnetic properties of the conventional R-B-Fe alloy are due to NdzFe
It is explained that it is based on a zB-phase compound, and therefore many proposals for improving magnetic properties are based on compositions close to that corresponding to this compound, i.e., R-13 to 17%, B=5.
Based on experiments with alloys in the range ~8%.
希土類元素は高価であるため、その含有量を低下させる
ことが望まれるが、希土類元素の含有量が１３％未満に
なると、保磁力ｉＨｃが急激に劣化するという問題があ
る。すなわち、Ｒ−Ｂ −Ｆｅ合金において希土類元素
の含有量が１３％未満になり、Ｂ含有量が高くなると、
保磁力ｉＨｃが劣化するとの事実があったのであるが、
かかる組成範囲において保磁力ｉＨｃの劣化を防止する
ように組成ならびに組織を設計する方法は従来知られて
いなかった。Since rare earth elements are expensive, it is desirable to reduce their content, but when the content of rare earth elements becomes less than 13%, there is a problem that the coercive force iHc rapidly deteriorates. That is, when the rare earth element content in the R-B-Fe alloy becomes less than 13% and the B content increases,
There was a fact that the coercive force iHc deteriorated,
Conventionally, no method was known for designing the composition and structure so as to prevent deterioration of the coercive force iHc in such a composition range.
本発明者らは、Ｒ−Ｂ−Ｆｅ合金のＲ含有量を１３％未
満にし、Ｂ含有量を１５％超とした低Ｒ１高Ｂ組成のＲ
−Ｂ−Ｆｅ合金にＣＯを添加した組成において、−軸磁
気異方性を呈する（ Ｆ ｅｌ Ｃｏ） ｚ Ｂ型組が
関与した場合に高保磁力ｉＨｃが得られることを見出し
た。すなわち、この（Ｆｅ、Ｃｏ）ｚＢ型型組生成する
ように組成を限定すると、希土類元素含有量低下に伴う
保磁力ｉＨｃの劣化が防止され、従来最良の磁石特性が
得られていたＲ＝１３〜１７％、Ｂ＝５〜８％の範囲の
Ｒ−Ｂ−Ｆｅ合金と匹敵する磁石特性が得られることを
見出し本発明を完成した。The present inventors have developed an R-B-Fe alloy with a low R1 high B composition in which the R content is less than 13% and the B content is greater than 15%.
It has been found that in a composition in which CO is added to a -B-Fe alloy, a high coercive force iHc can be obtained when the (FelCo)zB type set exhibiting -axis magnetic anisotropy is involved. In other words, if the composition is limited to produce this (Fe, Co)zB type set, the deterioration of the coercive force iHc due to the decrease in the rare earth element content is prevented, and R = 13, which had conventionally provided the best magnetic properties. The present invention was completed by discovering that magnetic properties comparable to those of an R-B-Fe alloy in which B is 17% and B is 5 to 8% can be obtained.
すなわち、本発明は、ＲｚＢｖ（Ｆｅ１−ｕ−ｗｃＯｗ
Ｍｕ） ＋−＊−ｖ（但し、０．０２≦Ｚ≦０．２．０
．１５＜ ＶＳ２．４．０〈Ｕ≦０．３．０．０５≦ｗ
≦０．５であり、またＲはＹを含む希土類元素、Ｍは、
ＡＩ、Ｔｉ、Ｃ，Ｓｉ、Ｐ、Ｖ、Ｃｒ、Ｍｎ。That is, the present invention provides RzBv(Fe1-u-wcOw
Mu) +-*-v (however, 0.02≦Z≦0.2.0
．． 15<VS2.4.0<U≦0.3.0.05≦w
≦0.5, R is a rare earth element containing Y, M is
AI, Ti, C, Si, P, V, Cr, Mn.
Ｚｒ、Ｈｆ 、Ｎｔ＋＋ Ｔａ ＋ Ｍｏ、 Ｇｅ、
Ｎ ｔ ＋ Ｗ＋ Ｃｕ 、およびＡｇの少なくとも１
種である）よりなり、（Ｆｅ、Ｃｏ）ｚＢ型型組含む組
織を有し、かつ高い保磁力を有することを特徴とする磁
石合金である。Zr, Hf, Nt++ Ta + Mo, Ge,
N t + W + Cu, and at least one of Ag
It is a magnetic alloy characterized by having a structure containing a (Fe, Co)zB type structure, and having a high coercive force.
以下、本発明のＲ−Ｂ−Ｆｅ合金の組成限定理由を説明
する。The reasons for limiting the composition of the R-B-Fe alloy of the present invention will be explained below.
ｚ （Ｒの原子数）を０．２以下に定めたのは、これを
越えると残留磁束密度が低下するからである。The reason why z (the number of atoms of R) is set to 0.2 or less is that if it exceeds this, the residual magnetic flux density will decrease.
２が０．０２未満であると角型比および保磁力が低下す
るため、Ｚは０．０２以上とした。好ましい希土類元素
Ｒの含有量は０．０３≦Ｚ ＜ ０．１である。より好
ましい希土類元素Ｒの含有量は０．０３≦ｚ＜０．０８
である。Ｂの含有量Ｖが０．１５以下であると保磁力が
低下し、一方Ｖが０．４を越えると残留磁束密度が低下
するため、ＶＳ０．１５超〜０．４とした。ＣＯはキュ
リ一点を上昇しかつ残留磁束密度の温度特性を改良する
元素である。Ｃｏの含有量Ｗが０．０５未満では一軸異
方性を有する強磁性（Ｆｅ、Ｃｏ）ｚＢ型型組生成させ
ることができず、一方Ｗが０．５を越えると保磁力ｉＨ
ｃが低下するため、ｗ＝０．０５〜０．５とした。好ま
しいＣＯ含有量は０．１≦ｗ≦０．４である。Ｍは保磁
力ｉＨｃを向上する元素である。Ｍの含有Ｊｉｕ（Ｆｅ
、ＣｏとＭの合計原子数を１としたときのＭの原子数）
が０．３を越えると、残留磁束密度が低下するのでＵ≦
０．３とした。好ましいＭの含有量ｕは０．０１〜０．
１５である。If Z is less than 0.02, the squareness ratio and coercive force will decrease, so Z is set to 0.02 or more. The content of the rare earth element R is preferably 0.03≦Z<0.1. The more preferable rare earth element R content is 0.03≦z<0.08
It is. If the B content V is 0.15 or less, the coercive force will decrease, while if V exceeds 0.4, the residual magnetic flux density will decrease, so VS was set to be more than 0.15 to 0.4. CO is an element that increases the Curie point and improves the temperature characteristics of the residual magnetic flux density. If the Co content W is less than 0.05, a ferromagnetic (Fe, Co)zB type mold with uniaxial anisotropy cannot be generated, while if W exceeds 0.5, the coercive force iH
Since c decreases, w was set to 0.05 to 0.5. The preferred CO content is 0.1≦w≦0.4. M is an element that improves coercive force iHc. M content Jiu(Fe
, the number of atoms of M when the total number of atoms of Co and M is 1)
When exceeds 0.3, the residual magnetic flux density decreases, so U≦
It was set to 0.3. The preferable M content u is 0.01 to 0.
It is 15.
次に、本発明のＲ−Ｂ−Ｆｅ合金の組織について説明す
る。Next, the structure of the R-B-Fe alloy of the present invention will be explained.
本発明は、従来のＲｔＦｅ、 、Ｂ型磁石合金と異なり
、低希土類元素Ｒ量、高Ｂ域に組成があり、かかる組成
域においては（Ｆｅ、Ｃｏ）ｚＢ型型組含む組織である
場合に高い保磁力ｉＨｃが得られることを見出したもの
である。この（Ｆｅ、Ｃｏ）ｚＢ型型組しては、（Ｆｅ
、Ｇｏ）ｔＢに一部添加元素Ｍが含有され、Ｆｅ、Ｇｏ
またはＢを一部置換した相、および（Ｆｅ、 Ｃｏ）
ＪＲｏ、 ＋ ７と表わされ、さらに希土類元素Ｒが一
部に含有される相も包含される。（Ｆ ｅｌ ＣＯ）
Ｚ Ｂ相はＭ元素の置換量にもよるが、ａ＝約５オング
ストローム、Ｃ＝約４オングストロームの格子定数を有
する正方晶構造を示し、Ｃ軸方向に高い一軸異方性を有
する、キュリ一点が約１１００にの化合物である。また
、（Ｆｅ＋Ｃｏ）ＪＲｏ、 ｌ？はＭ元素の置換量にも
より異なるが、ａ＝約９．５オングストローム、Ｃ＝約
７．５オングストロームの格子定数を有する大方晶構造
を示し、キュリ一点が約６００ Ｋの化合物である。共
存しうる他の相としては、組成にもよるが、ＮｄＪｅ＋
４８． Ｆｅ、 ＦｅＪ＋ ＲＪｅｔＪ＊＋ １Ｊｄ
ＰｅＪ４が確認された。The present invention differs from conventional RtFe, , and B type magnet alloys in that it has a composition in a low rare earth element R content and high B range, and in this composition range, it has a structure containing (Fe, Co)zB type structure. It was discovered that a high coercive force iHc can be obtained. This (Fe, Co)zB type assembly is (Fe, Co)
, Go) tB partially contains the additive element M, and Fe, Go
or a phase in which B is partially substituted, and (Fe, Co)
It is expressed as JRo, +7, and also includes a phase in which the rare earth element R is partially contained. (Fel CO)
The Z B phase exhibits a tetragonal structure with lattice constants of a = approximately 5 angstroms and C = approximately 4 angstroms, depending on the substitution amount of the M element, and has a single Curie point with high uniaxial anisotropy in the C-axis direction. is about 1100 compounds. Also, (Fe+Co)JRo, l? Although it varies depending on the amount of substitution of the M element, it is a compound that exhibits an orthogonal structure with lattice constants of a=about 9.5 angstroms and C=about 7.5 angstroms, and a single Curie point of about 600 K. Other phases that can coexist include NdJe+, although it depends on the composition.
48. Fe, FeJ+ RJetJ*+ 1Jd
PeJ4 was confirmed.
続いて、本発明のＲ−Ｂ−Ｆｅ合金の磁石特性について
説明する。上述したように組成および組織を特定するこ
とにより、約６ ｋＯｅ以上の保磁力ｉＨｃが得られる
。一方、本発明と同様に希土類元素の含有量が低くかつ
Ｂ含有量が高いＲ−Ｂ−Ｆｅ合金にＣｏを所定量添加せ
ず、（Ｆｅ、Ｃｏ）ｚＢ含有組織としないならば、保磁
力ｉＨｃは２〜３ ｋｏｅと著しく低い値となり、永久
磁石として使用できるＲ−Ｂ−Ｆｅ合金は得られない。Next, the magnetic properties of the R-B-Fe alloy of the present invention will be explained. By specifying the composition and structure as described above, a coercive force iHc of about 6 kOe or more can be obtained. On the other hand, if a predetermined amount of Co is not added to the R-B-Fe alloy, which has a low rare earth element content and a high B content, as in the present invention, and the (Fe, Co)zB-containing structure is not formed, the coercive force The iHc becomes a significantly low value of 2 to 3 koe, and an R-B-Fe alloy that can be used as a permanent magnet cannot be obtained.
さらに、残留磁束密度Ｂｒが良好なことに加えて、保磁
力ｉＨｃの温度特性が良好になる。具体的には室温〜１
２０℃においてその変化率が０．０５〜０、１％／℃と
なる。これは、本発明のＲ−Ｂ −Ｆｅ合金は希土類元
素の含有量低下に伴って、鉄およびコバルトの含有量が
高くなったためである。Furthermore, in addition to the residual magnetic flux density Br being good, the temperature characteristics of the coercive force iHc are also good. Specifically, room temperature ~ 1
At 20°C, the rate of change is 0.05 to 0.1%/°C. This is because in the R-B-Fe alloy of the present invention, the content of iron and cobalt increased as the content of rare earth elements decreased.
上述したごとき本発明のＲ−Ｂ−Ｆｅ合金は、液体急冷
法、焼結法、ホットプレス法、樹脂結合法、鋳造法など
により製造される。The R-B-Fe alloy of the present invention as described above is manufactured by a liquid quenching method, a sintering method, a hot pressing method, a resin bonding method, a casting method, or the like.
Ｒ−Ｂ −Ｆｅ合金のＢ含有量が保磁力１ｔｌｃに及ぼ
す影響を調査する実験を行なった。供試したＲ −Ｂ
−Ｆｅ合金の組成は下記のとおりであった。An experiment was conducted to investigate the influence of the B content of the R-B-Fe alloy on the coercive force 1tlc. Tested R-B
The composition of the -Fe alloy was as follows.
希土皿豆皇凡ｊＬｔＬｆｊｔＭ豆素 ハ販５％Ｎ６
５〜４０％ Ｎｂ２．５％ Ｆｅｏ、ｔＣｏｏ、
１（残部）５％Ｎｄ５〜４０％ Ｚｒ２．５％ Ｆｅｏ
、７Ｃｏｏ、３（残部）５％Ｎｄ５〜４０％ −Ｆｅｃ
＋、７ＣＯｏ、３（残部）５％Ｎｄ５〜４０％ −Ｆｅ
（残部）所定組成のインゴットを溶解により製
造し、これを小片に砕き、得られた粉末を溶解し、片ロ
ール法を用いた液体急冷法によりロールの表面速度を１
０〜４Ｑｍ／ｓｅｃで変化させて、リボン状試料を製造
した。保磁力ｉＨｃが最大になるロールの表面速度にお
いて得られた試料の保磁力１１１ｃとＢ含有量との関係
を第１図に示す。第１図より次の点が明らかとなる。Rare Earthen Plate Bean Soup 5%N6
5-40% Nb2.5% Feo, tCoo,
1 (remainder) 5% Nd 5-40% Zr 2.5% Feo
, 7Coo, 3 (remainder) 5%Nd5~40% -Fec
+, 7COo, 3 (remainder) 5%Nd5-40% -Fe
(Remaining part) An ingot with a predetermined composition is produced by melting, this is crushed into small pieces, the obtained powder is melted, and the surface speed of the roll is reduced to 1 by the liquid quenching method using the single roll method.
Ribbon-shaped samples were manufactured by varying the speed from 0 to 4 Qm/sec. FIG. 1 shows the relationship between the coercive force 111c and the B content of the sample obtained at the surface speed of the roll where the coercive force iHc becomes maximum. The following points become clear from Figure 1.
（１）Ｃｏの添加により、最大保磁力ｉＨｃが得られる
Ｂ含有量は高目に移る。(1) By adding Co, the B content at which the maximum coercive force iHc is obtained shifts to a higher level.
（２）Ｃｏの添加がない場合、Ｂ含有量の調節によって
最大保磁力ｉＨｃが得られるようにしても、得られる保
磁力ｉＨｃは極めて低い。(2) In the absence of Co addition, even if the maximum coercive force iHc is obtained by adjusting the B content, the obtained coercive force iHc is extremely low.
（３）Ｃｏの添加とＢ含有量の高目設定（Ｂ＝１５〜４
０％）の二つの条件がともに満足されて初めて、保磁力
ｉＨｃの向上効果が生じる。(3) Addition of Co and setting of high B content (B = 15 to 4
The effect of improving the coercive force iHc occurs only when both of the two conditions (0%) are satisfied.
（４）Ｍ元素として添加されるＮｂ、Ｚｒは、上記（３
）による効果にさらに保磁力ｉＨｃの向上効果を附加す
る。(4) Nb and Zr added as M elements are
), the effect of improving the coercive force iHc is added.
上記した（１）〜（４）より、優れた保磁力ｉＨｃ、を
得るためのＣｏ、Ｂおよび希土類元素Ｒの含有量は相互
に関係しており、低めの希土類元素Ｒでかつ高めのＢの
含有範囲にＣｏを添加することが必要であることが分か
る。なお、この組成範囲はＮｄＪ１３＋ａＢ相の生成組
成範囲から低段側に偏位しているので、磁石特性上は好
ましくない範囲であるが、（Ｆ ｅ、 ＣＯ） ２ Ｂ
整相を生成させることによりＮｄｚＦｅ＋Ｊ相生成量減
少を補って余りある磁石特性の向上を達成することがで
きる。From (1) to (4) above, the contents of Co, B, and rare earth element R to obtain an excellent coercive force iHc are related to each other. It can be seen that it is necessary to add Co within the content range. Note that this composition range deviates to the lower side from the composition range in which the NdJ13+aB phase is formed, so it is an unfavorable range in terms of magnetic properties, but (Fe, CO) 2 B
By generating phasing, it is possible to achieve an improvement in the magnetic properties that more than compensates for the decrease in the amount of NdzFe+J phase generated.
本発明のＲ−Ｂ−Ｆｅ合金は低い希土類元素含有量で優
れた保磁力ｉＨｃを達成するために、原料コストが低減
される。さらに、本発明のＲ−Ｂ−Ｆｅ合金は残留磁束
密度の温度特性が優れている。The R-B-Fe alloy of the present invention achieves excellent coercivity iHc with low rare earth element content, thus reducing raw material cost. Furthermore, the R-B-Fe alloy of the present invention has excellent temperature characteristics of residual magnetic flux density.
以下、さらに実施例により本発明を説明する。 The present invention will be further explained below with reference to Examples.
なお、本説明において使用されている百分率シよすべて
原子％によるものである。Note that all percentages used in this description are based on atomic %.
実施例１
第１表に組成を示すインゴットを溶解法により製造し、
インゴットを小片に砕き、これを片ロールを用いた液体
急冷法によりロールの表面速度を１０〜４０ｍ／ｓｅｃ
変化させてリボン状の試料を製造した。保磁力（ＩＨＯ
）が最大となるロールの表面速度において得られた試料
の磁石特性を第１表に示す。Example 1 An ingot whose composition is shown in Table 1 was produced by a melting method,
The ingot is crushed into small pieces, and then the surface speed of the roll is set at 10 to 40 m/sec using a liquid quenching method using a single roll.
Ribbon-shaped samples were produced with variations. Coercive force (IHO
Table 1 shows the magnetic properties of the samples obtained at the surface speed of the roll at which .
（以下、余白）
第１表
第１表続き
第１表続き
第１表より、本発明のＲ−Ｂ−Ｆｅ合金は、希土類元素
Ｒの含有量が高い従来のＲ−Ｂ −Ｆｅ合金と同等の磁
石特性を有することが分かる。(Hereinafter, blank spaces) Table 1 Table 1 continued Table 1 continued From Table 1, the R-B-Fe alloy of the present invention is equivalent to the conventional R-B-Fe alloy with a high content of rare earth element R. It can be seen that the magnet has the following magnetic properties.
実施例２
２３Ｂ−１，２Ｚｒ−１，２Ｎｂ−５Ｎｄ−２０Ｃｏ−
２Ｃ−４７，６Ｆｅ組成合金を高周波溶解炉により溶解
し金型に鋳造した。得られた鋳塊の寸法はφ２０Ｘ１５
ｍであった。端面を水冷した金型により凝固中の冷却を
制御した。Example 2 23B-1,2Zr-1,2Nb-5Nd-20Co-
A 2C-47,6Fe composition alloy was melted in a high frequency melting furnace and cast into a mold. The dimensions of the obtained ingot are φ20×15
It was m. Cooling during solidification was controlled by a mold with water-cooled end surfaces.
得られた鋳塊に５００℃で時効処理を施した。得られた
磁石特性はＢｒ ＝ ９．２ＫＧ 、 ＋Ｈｏ＝１１Ｋ
Ｏｅ 。The obtained ingot was subjected to aging treatment at 500°C. The obtained magnetic properties are Br = 9.2KG, +Ho = 11K
Oe.
（ＢＨ）□−＝ １８ＭＧＯｅであった。比較例として
８Ｂ−１，２Ｚｒ−１，２Ｎｂ−５Ｎｄ−２０Ｃｏ−２
Ｃ−４７，６Ｆｅ合金を同様な条件で作成した所、Ｂｒ
−７，２ＫＧ、＋Ｈｏ＝３．０゜（ＢＨ）、、、 ＝
３ ＭＧＯｅであった。(BH)□-=18MGOe. 8B-1,2Zr-1,2Nb-5Nd-20Co-2 as a comparative example
When C-47,6Fe alloy was prepared under similar conditions, Br
-7,2KG, +Ho=3.0゜(BH),,, =
3 MGOe.
第１図は保磁力１）１ｃとＢ含有量との関係を示すグラ
フである。FIG. 1 is a graph showing the relationship between coercive force 1) 1c and B content.
Claims (1)
Ｍ＿ｕ）＿１＿−＿ｚ＿−＿ｖ（但し、０．０２≦Ｚ≦
０．２、０．１５＜ｖ≦０．４、０＜ｕ≦０．３、０．
０５≦ｗ≦０．５であり、またＲはＹを含む希土類元素
、Ｍは、Ａｌ、Ｔｉ、Ｃ、Ｓｉ、Ｐ、Ｖ、Ｃｒ、Ｍｎ、
Ｚｒ、Ｈｆ、Ｎｂ、Ｔａ、Ｍｏ、Ｇｅ、Ｎｉ、Ｗ、Ｃｕ
、およびＡｇの少なくとも１種である）よりなり、（Ｆ
ｅ、Ｃｏ）＿２Ｂ型相を含む組織を有し、かつ高い保磁
力を有することを特徴とする磁石合金。1, R_zB_v(Fe_1_-_u_-_wCo_w
M_u)_1_-_z_-_v (However, 0.02≦Z≦
0.2, 0.15<v≦0.4, 0<u≦0.3, 0.
05≦w≦0.5, R is a rare earth element containing Y, M is Al, Ti, C, Si, P, V, Cr, Mn,
Zr, Hf, Nb, Ta, Mo, Ge, Ni, W, Cu
, and Ag), and (F
A magnetic alloy characterized by having a structure including e, Co)_2B type phase and having a high coercive force.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61315824A JPS63169357A (en) | 1986-12-29 | 1986-12-29 | Magnetic alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61315824A JPS63169357A (en) | 1986-12-29 | 1986-12-29 | Magnetic alloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS63169357A true JPS63169357A (en) | 1988-07-13 |
Family
ID=18070002
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP61315824A Pending JPS63169357A (en) | 1986-12-29 | 1986-12-29 | Magnetic alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS63169357A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0257662A (en) * | 1988-08-23 | 1990-02-27 | M G:Kk | Rapidly cooled thin strip alloy for bond magnet |
-
1986
- 1986-12-29 JP JP61315824A patent/JPS63169357A/en active Pending
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0257662A (en) * | 1988-08-23 | 1990-02-27 | M G:Kk | Rapidly cooled thin strip alloy for bond magnet |
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