JPS6324042A - Rare earth metal-base amorphous alloy and its production - Google Patents
Rare earth metal-base amorphous alloy and its productionInfo
- Publication number
- JPS6324042A JPS6324042A JP61056679A JP5667986A JPS6324042A JP S6324042 A JPS6324042 A JP S6324042A JP 61056679 A JP61056679 A JP 61056679A JP 5667986 A JP5667986 A JP 5667986A JP S6324042 A JPS6324042 A JP S6324042A
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- amorphous
- hydrogen
- absorption reaction
- hydrogen absorption
- 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.)
- Granted
Links
- 229910000808 amorphous metal alloy Inorganic materials 0.000 title claims abstract description 19
- 229910052761 rare earth metal Inorganic materials 0.000 title claims abstract description 10
- 150000002910 rare earth metals Chemical class 0.000 title claims abstract description 7
- 238000004519 manufacturing process Methods 0.000 title claims description 10
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 claims abstract description 69
- 239000001257 hydrogen Substances 0.000 claims abstract description 62
- 229910052739 hydrogen Inorganic materials 0.000 claims abstract description 62
- 238000010521 absorption reaction Methods 0.000 claims abstract description 41
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 29
- 239000000956 alloy Substances 0.000 claims abstract description 29
- 229910000765 intermetallic Inorganic materials 0.000 claims abstract description 8
- 229910052742 iron Inorganic materials 0.000 claims abstract description 7
- 239000000203 mixture Substances 0.000 claims abstract description 4
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 4
- 229910052747 lanthanoid Inorganic materials 0.000 claims abstract 3
- 150000002602 lanthanoids Chemical class 0.000 claims abstract 3
- 238000000034 method Methods 0.000 claims description 13
- 239000011261 inert gas Substances 0.000 claims description 8
- 238000000137 annealing Methods 0.000 claims description 5
- 239000007788 liquid Substances 0.000 claims description 5
- 238000004544 sputter deposition Methods 0.000 claims description 4
- 239000010409 thin film Substances 0.000 claims description 4
- 238000005096 rolling process Methods 0.000 claims description 3
- 229910052706 scandium Inorganic materials 0.000 claims description 2
- 238000007740 vapor deposition Methods 0.000 claims description 2
- 238000001816 cooling Methods 0.000 claims 1
- 230000005415 magnetization Effects 0.000 abstract description 8
- 150000001875 compounds Chemical class 0.000 abstract description 4
- 239000007787 solid Substances 0.000 abstract description 3
- 239000000843 powder Substances 0.000 description 13
- 239000012300 argon atmosphere Substances 0.000 description 10
- 229910052751 metal Inorganic materials 0.000 description 7
- 239000002184 metal Substances 0.000 description 7
- 238000004458 analytical method Methods 0.000 description 6
- 239000000155 melt Substances 0.000 description 6
- 230000008018 melting Effects 0.000 description 6
- 238000002844 melting Methods 0.000 description 6
- 238000002441 X-ray diffraction Methods 0.000 description 5
- 125000004429 atom Chemical group 0.000 description 3
- 238000010791 quenching Methods 0.000 description 3
- 230000000171 quenching effect Effects 0.000 description 3
- 239000002994 raw material Substances 0.000 description 3
- 238000005280 amorphization Methods 0.000 description 2
- 229910001004 magnetic alloy Inorganic materials 0.000 description 2
- 150000002739 metals Chemical class 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000007254 oxidation reaction Methods 0.000 description 2
- 229910052684 Cerium Inorganic materials 0.000 description 1
- 229910052691 Erbium Inorganic materials 0.000 description 1
- 229910052693 Europium Inorganic materials 0.000 description 1
- 229910052688 Gadolinium Inorganic materials 0.000 description 1
- 229910052689 Holmium Inorganic materials 0.000 description 1
- 229910052765 Lutetium Inorganic materials 0.000 description 1
- 229910052779 Neodymium Inorganic materials 0.000 description 1
- 229910052777 Praseodymium Inorganic materials 0.000 description 1
- 229910052771 Terbium Inorganic materials 0.000 description 1
- 229910052769 Ytterbium Inorganic materials 0.000 description 1
- 229910002091 carbon monoxide Inorganic materials 0.000 description 1
- 239000003054 catalyst Substances 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 238000011109 contamination Methods 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 238000000227 grinding Methods 0.000 description 1
- 238000000265 homogenisation Methods 0.000 description 1
- 150000002431 hydrogen Chemical class 0.000 description 1
- 229910052746 lanthanum Inorganic materials 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 238000010298 pulverizing process Methods 0.000 description 1
- 229910052727 yttrium Inorganic materials 0.000 description 1
Landscapes
- Physical Vapour Deposition (AREA)
Abstract
Description
【発明の詳細な説明】
本発明は希土類元素全含む非晶質合金およびその製造方
法に関するものであり、特に結晶質合金あるいは金属間
化合物に水素吸収反応を施し非晶質化させることを特徴
とする。[Detailed Description of the Invention] The present invention relates to an amorphous alloy containing all rare earth elements and a method for producing the same, and is particularly characterized by subjecting a crystalline alloy or an intermetallic compound to a hydrogen absorption reaction to make it amorphous. do.
従来の非晶質合金の製造方法としては、液体急冷法、ス
パッタ法な゛どそれぞれ液体あるいは気体からの製造方
法が知られている。（たとえば、アモルファス金属の基
礎：増重 健編著、オーム社）。一方、最近になって結
晶質合金に水素全吸収させると非晶質化することが報告
されている。しかし、本発明の出願前の研究報告によれ
ば、ＳｍＮ ｉ ｚ、 ＧｄＮ ｉ ２など希土類元素
−ニッケル系に限られており、磁気的性質などの応用に
おいて有利なＦｅ、ＣＯヲ含有する合金系は知られてい
なかった。Conventional methods for manufacturing amorphous alloys include liquid quenching, sputtering, and other methods using liquids or gases, respectively. (For example, Basics of Amorphous Metals: edited by Ken Masashige, Ohmsha). On the other hand, it has recently been reported that when a crystalline alloy is made to completely absorb hydrogen, it becomes amorphous. However, according to research reports prior to the filing of the present invention, it is limited to rare earth element-nickel systems such as SmN i z and GdN i 2, and alloy systems containing Fe and CO, which are advantageous in applications such as magnetic properties, are was unknown.
これに対して、本発明者らは磁気的性質などの応用にお
いて有利なＦｅ、Ｃｏ’ｉ含有する希土類元素の合金あ
るいは化合物が水素吸収反応によって非晶質化すること
を新た見出し、本発明を完成した。この合金はまた水素
全含有するため酸化しがたい特徴がある。また、不発明
の非晶質合金の製造方法は、結晶固体から直接非晶質固
体を得ること全可能にするもので、非晶質合金を容易に
大量かつ均一に製造でき、コストの低減にも役立つとい
う有利な方法である。従来の液体急冷法、スパッタ法で
は薄帯あるいは薄膜という形状的な制約があったが、本
発明の製造方法によれば非晶質合金塊を直線に製造しう
るという点で従来の形状的制約を取り除いたという利点
がある。さらに非晶質合金塊を粉砕することによシ非晶
質粉末？容易に作製することができ、この非晶質合金粉
末に温間で加圧成型などの処理を施すことにより強度の
高い非晶質合金塊を製造することもできる。また粉砕に
よシ得られた非晶質超微粉末はテープなどに塗布して使
用できるし、蒸着あるいはスパッタ法などにより作製し
た結晶質薄膜に水素を吸収させて非晶質合金薄膜を作る
こともできる。さらに水素吸収反応の前処理として特許
請求の範囲第３項および第４項に示す条件の下で均一化
焼鈍あるいは液体急冷を施すことにより、続く水素吸収
反応による非晶質化の時間を大幅に短縮できる。In contrast, the present inventors have newly discovered that alloys or compounds of rare earth elements containing Fe and Co'i, which are advantageous in applications such as magnetic properties, become amorphous through a hydrogen absorption reaction, and have developed the present invention. completed. This alloy also has the characteristic of being resistant to oxidation since it contains all hydrogen. In addition, the uninvented method for producing amorphous alloys makes it possible to obtain amorphous solids directly from crystalline solids, making it possible to easily produce amorphous alloys in large quantities and uniformly, reducing costs. This is an advantageous method that also helps. Conventional liquid quenching methods and sputtering methods had shape constraints such as thin strips or thin films, but the production method of the present invention overcomes the traditional shape limitations in that an amorphous alloy lump can be produced in a straight line. It has the advantage of removing . By further grinding the amorphous alloy lump into amorphous powder? It can be easily produced, and a high-strength amorphous alloy ingot can also be produced by subjecting this amorphous alloy powder to a treatment such as warm pressure molding. In addition, the amorphous ultrafine powder obtained by pulverization can be used by coating it on a tape, etc., or an amorphous alloy thin film can be made by absorbing hydrogen into a crystalline thin film made by vapor deposition or sputtering. You can also do it. Furthermore, by performing homogenization annealing or liquid quenching under the conditions shown in claims 3 and 4 as a pretreatment for the hydrogen absorption reaction, the time required for amorphization by the subsequent hydrogen absorption reaction can be significantly reduced. Can be shortened.
なお、Ｒ（Ｆ ｅｘ Ｃｏｙ Ｎｉｚ ）ｎにおいてｎ
＜Ｑ、２あるいはｎ＞５の場合には、本発明の方法によ
シ好ましい非晶質合金は得られなかった。また、製造条
件として水素の圧力が１５０気圧以上でも非晶質合金を
得ることができるが、圧力上昇による危険性などのデメ
リットにみあうメリットがないので１５０気圧以下で行
うことが好まなるので２７３〜１２７３にの温度範囲に
限定した。Note that in R(F ex Coy Niz )n, n
In the case of <Q, 2 or n>5, a preferred amorphous alloy could not be obtained by the method of the present invention. In addition, although it is possible to obtain an amorphous alloy even if the hydrogen pressure is 150 atm or more as a manufacturing condition, it is preferable to carry out the process at 150 atm or less because there is no advantage to outweigh the disadvantages such as the risk of increased pressure. The temperature range was limited to 1273°C.
水素吸収反応の偏置としては２７３に以下では長時間の
処理を必要とし７７３に以上では酸化などによる試料の
汚染が問題になるので２７３〜７７３にの温度範囲に限
定した。水素吸収反応において水素量が０．１原子チ以
下では非晶質化せず、また、０．８原子チ以上の水素は
吸収されなかったので０．１〜０，８チに限定した。以
上の本発明における非晶質合金は、たとえば高記録密度
の光磁気ディスク装置の記録媒体、センサーおよび触媒
などに応用される。The temperature range for the hydrogen absorption reaction was limited to a temperature range of 273 to 773, since temperatures below 273 would require a long treatment time, and temperatures above 773 would cause problems with sample contamination due to oxidation. In the hydrogen absorption reaction, if the amount of hydrogen was less than 0.1 atoms, it did not become amorphous, and hydrogen in amounts of more than 0.8 atoms was not absorbed, so it was limited to 0.1 to 0.8 atoms. The amorphous alloy of the present invention described above is applied, for example, to recording media, sensors, catalysts, etc. of high-density magneto-optical disk drives.
実施例１
希土類元素としてＬａ、 Ｃｅ、 Ｐｒ、 Ｎｄ、Ｐ
ｍ、 Ｓｍ。Example 1 La, Ce, Pr, Nd, P as rare earth elements
m, Sm.
Ｅｕ、 Ｇｄ、 Ｔｂ、 Ｄ７、Ｈｏ、Ｅｒ、Ｔｒｎ、
Ｙｂ、 Ｌｕ、 Ｓｃ、Ｙを含有した特許請求の範
囲第１項における合金に水素吸収反応音節した結果、非
晶質であることが確認できた。これを第１表にまとめて
示す。Eu, Gd, Tb, D7, Ho, Er, Trn,
As a result of conducting a hydrogen absorption reaction on the alloy in claim 1 containing Yb, Lu, Sc, and Y, it was confirmed that the alloy was amorphous. This is summarized in Table 1.
第１表
実施例２
ＤｙＦｅ２ｆアルゴン雰囲気下のアーク溶解によって３
０ｇ溶製した。ここで原料金属の純度は、Ｄｙ：９９．
９チ、Ｆｅ：９９．９９チであった。得られた合金塊ｉ
７２３Ｋ、５日間アルゴン雰囲気中（純度９９．９９
９％）で均一化焼鈍した後、１００メツシユ以下の粉末
にし水素吸収反応全行う試料にした。試料粉末１０ｇ’
ｅ水素吸収反応装置に入れて４７３にで１時間脱ガスし
た後、３２３Ｋまで冷却し、５０気圧の水素ガス（純度
９９．９９９９９％）を導入し２時間水素を吸収させた
。水素吸収反応後の試料の構造をＸ線回折装置（Ｃｕ対
陰極）で固定し、水素吸収反応後の試料の構造は非晶質
であること全確認した。また不活性ガス中溶融熱伝導法
により分析した結果、水素含有量は原子パーセントで０
．４ ％であった。Table 1 Example 2 DyFe2f 3 by arc melting under argon atmosphere
0g was melted. Here, the purity of the raw material metal is Dy:99.
9chi, Fe: 99.99chi. Obtained alloy ingot i
723K, 5 days in argon atmosphere (purity 99.99
After uniform annealing at 9%), the sample was made into a powder of 100 mesh or less and subjected to all hydrogen absorption reactions. Sample powder 10g'
e It was placed in a hydrogen absorption reactor and degassed for 1 hour at 473 degrees centigrade, then cooled to 323K, hydrogen gas (purity 99.99999%) at 50 atm was introduced, and hydrogen was absorbed for 2 hours. The structure of the sample after the hydrogen absorption reaction was fixed with an X-ray diffraction device (Cu anticathode), and it was completely confirmed that the structure of the sample after the hydrogen absorption reaction was amorphous. Furthermore, as a result of analysis using the melt heat conduction method in an inert gas, the hydrogen content was found to be 0 in atomic percent.
．． It was 4%.
実施例３
ＨｏＦｅ２１アルゴン雰囲気下のアーク溶解によって３
０ｇ溶製した。ここでｊ料金属の純度は、Ｈａ ： ９
９．９％、Ｆ’ｅ：９９．９９％であった。得うレタ合
金塊ｆ ７７３Ｋ、５日間アルゴン雰囲気中（純度９９
．９９９％）で均一化焼鈍した後、１００メツシユ以下
の粉末にし水素吸収反応を行う試料にした。試料粉末１
０ｇを水素吸収反応装置に入れて４７３にで１時間脱ガ
スした後、３２３Ｋまで冷却し、５０気圧の水素ガス（
純度９９．９９９９９％）を導入し２時間水素を吸収さ
せた。水素吸収反応後の試料の構造をＸ線回折装置（Ｃ
ｕ対陰極）で固定し、水素吸収反応後の試料の構造は非
晶質であることを確認した。また不活性ガス中溶融熱伝
導法によ）分析した結果、水素含有量は原子パーセント
で０．３壬であった。Example 3 HoFe21 3 by arc melting under argon atmosphere
0g was melted. Here, the purity of the raw metal is Ha: 9
9.9%, F'e: 99.99%. Obtained Reta alloy ingot f 773K, 5 days in argon atmosphere (purity 99
．． After uniform annealing at 999%), the sample was made into a powder of 100 mesh or less and subjected to a hydrogen absorption reaction. Sample powder 1
0g was placed in a hydrogen absorption reactor and degassed for 1 hour at 473°C, cooled to 323K, and heated to 50 atmospheres of hydrogen gas (
(purity 99.99999%) was introduced and hydrogen was absorbed for 2 hours. The structure of the sample after the hydrogen absorption reaction was analyzed using an X-ray diffraction device (C
It was confirmed that the structure of the sample after the hydrogen absorption reaction was amorphous. Further, as a result of analysis (by the melt heat conduction method in an inert gas), the hydrogen content was 0.3 壬 in atomic percent.
実施例４
ＧｄＣｏｚ ｆアルゴン雰囲気下のアーク溶解によって
１５ｇ溶製した。ここで原料金属の純度は、Ｇｄ：９９
．９宏 ＣＯ：９９．９係であった。得られた合金塊を
１００メツシユ以下の粉末にし水素吸収反応を行う試料
にした。試料粉末２ｇｋ水素吸収反応装置に入れて７０
０にで０．５時間脱ガスし、１００気圧の水素（純度９
９．９９９９９％）を導入し２．５時間水素を吸収させ
た。水素吸収反応後の試料の構造をＸ線回折装置（Ｃｕ
対陰甑）で固定した。Example 4 15 g of GdCoz f was produced by arc melting in an argon atmosphere. Here, the purity of the raw metal is Gd: 99
．． 9 Hiroshi CO: He was in charge of 99.9. The obtained alloy ingot was made into a powder of 100 mesh or less and used as a sample for hydrogen absorption reaction. Put 2gk of sample powder into hydrogen absorption reactor and add 70
Degas for 0.5 hours at
9.99999%) was introduced and hydrogen was absorbed for 2.5 hours. The structure of the sample after the hydrogen absorption reaction was analyzed using an X-ray diffraction device (Cu
It was fixed with a countershade.
その結果を第１図に示す。この図から水素吸収反応後の
試料の構造は非晶質であることが確認できた。また不活
性ガス中溶融熱伝導法てより分析した結果、水素含有量
は原子パーセントで０．５チであった。The results are shown in FIG. From this figure, it was confirmed that the structure of the sample after the hydrogen absorption reaction was amorphous. Further, as a result of analysis using the melt heat conduction method in an inert gas, the hydrogen content was found to be 0.5 atomic percent.
実施例５
Ｇｄ（Ｃｏ Ｏ，２Ｎ ｉ Ｏ，８）２ζアルゴン雰囲
気下のアーク溶製した。ここで原料金属の純度は、Ｇｄ
：９９．９％、Ｃｏ：９９．９係、Ｎｔ：９９．９７チ
であった。得られた合金塊を＝１０７３Ｋ 、３時間真
空中１０−２Ｔｏｒｒで均一化焼鈍した後、１００メツ
シユ以下の粉末にし水素吸収反応を行う試料にした。試
料粉末３ｇを水素吸収反応装置に入れて４２３にで１時
間脱ガスした後、３２３Ｋまで冷却し、５０気圧の・水
素ガス（純度９９．９９９９９矛）を導入し２時間水素
を吸収させた。水素吸収反応後の試料の構造をＸ、線回
折装置（Ｃｕ対陰極）で同定した。その結果を第２図シ
て示す。この図から水素吸収反応後の試料の構造は非晶
質であることが確認でさた。また不活性ガス中溶融熱伝
導法により分析した結果、水素含有量は原子パーセント
で０．４％であった。Example 5 Gd(CoO,2N i O,8)2ζ was produced by arc melting in an argon atmosphere. Here, the purity of the raw material metal is Gd
: 99.9%, Co: 99.9%, Nt: 99.97%. The obtained alloy ingot was uniformly annealed at 1073 K in vacuum at 10 -2 Torr for 3 hours, and then made into powder of 100 mesh or less to prepare a sample for hydrogen absorption reaction. 3 g of the sample powder was placed in a hydrogen absorption reactor and degassed for 1 hour at 423 degrees Celsius, then cooled to 323K, hydrogen gas (purity 99.99999) at 50 atmospheres was introduced, and hydrogen was absorbed for 2 hours. The structure of the sample after the hydrogen absorption reaction was identified using an X-ray diffractometer (Cu anticathode). The results are shown in Figure 2. This figure confirms that the structure of the sample after the hydrogen absorption reaction is amorphous. Further, as a result of analysis by the melt heat conduction method in an inert gas, the hydrogen content was 0.4% in atomic percent.
実施例６
Ｇｄ（Ｆｅ Ｏ，６Ｎｉ Ｏ，４） ２ ｋアルゴン雰
囲気下のアーク溶解によって２５ｇ溶製した。ここで原
料金属の純度は、Ｇｄ：９９．９％、 Ｆ’ｅ：９９．
９９％、Ｎ１Ｈ９９，９７％であった。得られた合金塊
の一部４ｇをアルゴン雰囲気中単ロール法（２００ｍ直
径Ｃｕロール、３０００ｒｐｍ ）により超急冷した
。Example 6 25 g of Gd(Fe O, 6Ni O, 4) 2k was melted by arc melting in an argon atmosphere. Here, the purity of the raw metals is Gd: 99.9%, F'e: 99.
99%, N1H 99.97%. A portion of 4 g of the obtained alloy ingot was ultra-quenched in an argon atmosphere by a single roll method (200 m diameter Cu roll, 3000 rpm).
このものは全く非晶質化はしていないにの試料３ｇ’に
水素吸収反応装置に入れて５２３にで２時間脱ガスした
後、３２３Ｋまで冷却し、１５０気圧の水素ガス（純度
９９．９９％）全導入し１時間水素を吸収させた。水素
吸収反応後の試料の構造ｉＸＸ線回折装置 Ｃｕ対陰極
）で固定した。その結果全第３図に示す。この図から水
素吸収反応後の試料の構造は非晶質であることが確認で
きた。また不活性ガス中溶融熱伝導法により分析した結
果、水素含有量は原子パーセントで０．１０チであった
。This material was placed in a hydrogen absorption reactor with 3g' of sample, which had not become amorphous at all, and degassed at 523 degrees Celsius for 2 hours, cooled to 323K, and heated to 150 atmospheres of hydrogen gas (purity 99.99). %) was completely introduced and hydrogen was absorbed for 1 hour. Structure of sample after hydrogen absorption reaction iXX-ray diffractometer (Cu anticathode) was fixed. The results are shown in Figure 3. From this figure, it was confirmed that the structure of the sample after the hydrogen absorption reaction was amorphous. Further, as a result of analysis by the melt heat conduction method in an inert gas, the hydrogen content was 0.10 atomic percent.
実施例７
ＣｅＦｅ２ｉアルゴン雰囲気下のアーク溶解によって３
０ｇ溶製した。ここで原料金属の純度は、Ｃｅ ： ９
９．９％、Ｆ’ｅ：９９．９９％であった。得られた合
金塊’ｋ １０２３ Ｋ、５日間アルゴン雰囲気中（純
度９９．９９９％）で均一化焼鈍した後、１００メツシ
ユ以下の粉末にし水素吸収反応全行う試料にした。試料
粉末１０ｇを水素吸収反応装置に入れて４７３にで１時
間脱ガスした後、３２３Ｋまで冷却し、５０気圧の水素
ガス（純度９９．９９９９９％）全導入し２時間水素全
吸収させた。水素吸収反応後の試料の構造をＸ線回折装
置（Ｃｕ対陰極）で固定した。その結果全第４図に示す
。この図から水素吸収反応後の試料の構造は非晶質であ
ることが確認できた。また不活性ガス中溶融熱伝導法に
より分析した結果、水素含有量は原子パーセントで０．
２５％であった。この方法により作製した非晶質合金お
よび水素吸収前の合金の磁化を振動型磁化測定装置（Ｖ
ＳＭ）により測定した。その結果を第５図および第６図
に示す。Example 7 CeFe2i 3 by arc melting under argon atmosphere
0g was melted. Here, the purity of the raw material metal is Ce: 9
9.9%, F'e: 99.99%. The obtained alloy ingot was homogenized by annealing at 1023 K for 5 days in an argon atmosphere (purity 99.999%), and then made into a powder of 100 meshes or less to prepare a sample that underwent a complete hydrogen absorption reaction. 10 g of sample powder was placed in a hydrogen absorption reactor and degassed at 473 for 1 hour, then cooled to 323 K, hydrogen gas (purity 99.99999%) at 50 atm was completely introduced, and hydrogen was completely absorbed for 2 hours. The structure of the sample after the hydrogen absorption reaction was fixed using an X-ray diffraction device (Cu anticathode). The results are shown in Figure 4. From this figure, it was confirmed that the structure of the sample after the hydrogen absorption reaction was amorphous. Furthermore, as a result of analysis using the melt heat conduction method in an inert gas, the hydrogen content was found to be 0.0% in atomic percent.
It was 25%. The magnetization of the amorphous alloy prepared by this method and the alloy before hydrogen absorption was measured using a vibrating magnetization measuring device (V
SM). The results are shown in FIGS. 5 and 6.
第５図および第６図かられかるように水素吸収により非
晶質化した試料の磁化はそれぞれ８０（ｅｍｕ／ｇ）、
３（ｅｍｕ／ｇ）であった。このように水素吸収による
非晶質化により磁化は２７倍に増大した。したがって、
水素吸収反応により磁化の高い非晶質磁性合金全製造す
ることができる。As can be seen from Figures 5 and 6, the magnetization of the sample made amorphous by hydrogen absorption is 80 (emu/g), respectively.
3 (emu/g). As described above, magnetization increased 27 times due to amorphization due to hydrogen absorption. therefore,
All amorphous magnetic alloys with high magnetization can be produced by hydrogen absorption reactions.
第１図〜第４図は本発明の非晶質磁性合金のＸ線回折装
置（Ｃｕ対陰極）による固定した結果のグラフである。
第５図は本発明の非晶質合金の磁化を表わすグラフであ
る。
第６図は同一組成の結晶試料の磁化を表わすグラフであ
る。
第１図
第２図
第３図
Ｉクー
第４図1 to 4 are graphs showing the results of fixing the amorphous magnetic alloy of the present invention using an X-ray diffraction apparatus (Cu anticathode). FIG. 5 is a graph showing the magnetization of the amorphous alloy of the present invention. FIG. 6 is a graph showing the magnetization of crystal samples of the same composition. Figure 1 Figure 2 Figure 3 Figure 4
Claims (1)
イド元素と２１番Ｓｃ、３９番Ｙの１７種の希土類金属
元素の中から少くとも１種、ｘ、ｙ、ｚはＦｅ、Ｃｏ、
Ｎｉの原子比で、Ｆｅ、Ｃｏ、Ｎｉの少くとも１種、（
ただし、ｘ＋ｙ＋ｚ＝１、ｚ≠１、０．２≦ｎ≦５）の
組成からなる合金あるいは金属間化合物に水素吸収反応
を施し、水素を原子パーセントで０．１％〜０．８％吸
収させたことを特徴とする非晶質合金。 ２Ｒ（ＦｅｘＣｏｙＮｉｚ）ｎ Ｒは原子番号５７番Ｌａから７１番Ｌｕまでのランタノ
イド元素２１番Ｓｃ、３９番Ｙの１７種の希土類金属元
素の中から少くとも１種ｘ、ｙ、ｚはＦｅ、Ｃｏ、Ｎｉ
の原子比で、Ｆｅ、Ｃｏ、Ｎｉの少くとも１種、（ただ
し、Ｘ＋ｙ＋Ｚ＝１、ｚ≠１、０．２≦ｎ≦５）の組成
からなる合金あるいは金属間化合物を２７３Ｋ以上７７
３Ｋ以下、で水素吸収反応を施すことにより非晶質化さ
せることを特徴とする非晶質合金の製造方。 ３特許請求の範囲第１項における合金あるいは金属間化
合物を不活性ガス雰囲気中あるいは真空度１０＾−＾２
Ｔｏｒｒ以上の真空中で、単ロール法あるいは双ロール
法などにより液体急冷を施した後、２７３Ｋ以上７７３
Ｋ以下、水素ガス圧力１５０気圧以下の条件で水素吸収
反応を施すことにより非晶質化させることを特徴とする
非晶質合金の製造方法。 ４特許請求の範囲第１項における合金あるいは金属間化
合物を不活性ガス雰囲気中あるいは真空度１０＾−＾２
Ｔｏｒｒ以上の真空中で、２７３Ｋ−１２７３Ｋの温度
範囲で均一化焼鈍した後、２７３Ｋ以上７７３Ｋ以下、
水素ガス圧力 １５０気圧以下の条件で水素吸収反応を施すことにより
非晶質化させることを特徴とする非晶質合金の製造方法
。 ５特許請求の範囲第１項における合金あるいは金属間化
合物を蒸着あるいはスパッタ法などにより薄膜化した後
、２７３Ｋ以上７７３Ｋ以下、水素ガス圧力１５０気圧
以下の条件で水素吸収反応を施すことにより非晶質化さ
せることを特徴とする非晶質合金の製造方法。[Scope of Claims] 1R(FexCoyNiz)n R is at least one element selected from 17 kinds of rare earth metal elements of lanthanide elements with atomic numbers 57 La to 71 Lu, 21 Sc, 39 Y, x , y, z are Fe, Co,
The atomic ratio of Ni is at least one of Fe, Co, and Ni, (
However, if an alloy or intermetallic compound having the composition x+y+z=1, z≠1, 0.2≦n≦5 is subjected to a hydrogen absorption reaction, 0.1% to 0.8% of hydrogen is absorbed in atomic percent. An amorphous alloy characterized by: 2R (FexCoyNiz)n R is a lanthanide element with atomic number No. 57 La to No. 71 Lu. At least one element from among the 17 rare earth metal elements No. 21 Sc and No. 39 Y. x, y, and z are Fe, Co. ,Ni
An alloy or intermetallic compound consisting of at least one of Fe, Co, and Ni (X+y+Z=1, z≠1, 0.2≦n≦5) with an atomic ratio of 273K or more, 77
A method for producing an amorphous alloy, characterized in that it is made amorphous by subjecting it to a hydrogen absorption reaction at 3K or less. 3. The alloy or intermetallic compound in claim 1 is prepared in an inert gas atmosphere or at a vacuum degree of 10^-^2.
After rapidly cooling the liquid by a single roll method or a twin roll method in a vacuum of Torr or more, the temperature is 773K or more.
A method for producing an amorphous alloy, characterized in that the alloy is made amorphous by performing a hydrogen absorption reaction under conditions of K or less and a hydrogen gas pressure of 150 atmospheres or less. 4. The alloy or intermetallic compound in claim 1 is prepared in an inert gas atmosphere or at a vacuum degree of 10^-^2.
After homogenizing annealing in a temperature range of 273K-1273K in a vacuum of Torr or more, 273K or more and 773K or less,
1. A method for producing an amorphous alloy, characterized in that the alloy is made amorphous by performing a hydrogen absorption reaction at a hydrogen gas pressure of 150 atmospheres or less. 5 The alloy or intermetallic compound in claim 1 is made into a thin film by vapor deposition or sputtering, and then amorphous is formed by subjecting it to a hydrogen absorption reaction under conditions of 273 K or more and 773 K or less and a hydrogen gas pressure of 150 atmospheres or less. 1. A method for producing an amorphous alloy, the method comprising:
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61056679A JPS6324042A (en) | 1986-03-14 | 1986-03-14 | Rare earth metal-base amorphous alloy and its production |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61056679A JPS6324042A (en) | 1986-03-14 | 1986-03-14 | Rare earth metal-base amorphous alloy and its production |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS6324042A true JPS6324042A (en) | 1988-02-01 |
| JPH0418022B2 JPH0418022B2 (en) | 1992-03-26 |
Family
ID=13034112
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP61056679A Granted JPS6324042A (en) | 1986-03-14 | 1986-03-14 | Rare earth metal-base amorphous alloy and its production |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS6324042A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4957824A (en) * | 1987-03-24 | 1990-09-18 | Kabushiki Kaisha Toshiba | Information storage medium and method of manufacturing the same |
| EP0643146A1 (en) * | 1993-09-14 | 1995-03-15 | Hitachi Chemical Co., Ltd. | Scandium containing hydrogen absorption alloy and hydrogen absorption electrode |
-
1986
- 1986-03-14 JP JP61056679A patent/JPS6324042A/en active Granted
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4957824A (en) * | 1987-03-24 | 1990-09-18 | Kabushiki Kaisha Toshiba | Information storage medium and method of manufacturing the same |
| EP0643146A1 (en) * | 1993-09-14 | 1995-03-15 | Hitachi Chemical Co., Ltd. | Scandium containing hydrogen absorption alloy and hydrogen absorption electrode |
| US5968450A (en) * | 1993-09-14 | 1999-10-19 | Hitachi Chemical Company, Ltd. | Scandium containing hydrogen absorption alloy and hydrogen absorption electrode |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0418022B2 (en) | 1992-03-26 |
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