JPS5842256B2 - amorphous alloy - Google Patents

amorphous alloy

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Publication number
JPS5842256B2
JPS5842256B2 JP54163656A JP16365679A JPS5842256B2 JP S5842256 B2 JPS5842256 B2 JP S5842256B2 JP 54163656 A JP54163656 A JP 54163656A JP 16365679 A JP16365679 A JP 16365679A JP S5842256 B2 JPS5842256 B2 JP S5842256B2
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Prior art keywords
amorphous
alloys
alloy
atomic
state
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JPS55107746A (en
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ホ・ソ−・チエン
ドナルド・エドワ−ド・ポルク
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ARAIDO CORP
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ARAIDO CORP
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    • H—ELECTRICITY
    • H05—ELECTRIC TECHNIQUES NOT OTHERWISE PROVIDED FOR
    • H05K—PRINTED CIRCUITS; CASINGS OR CONSTRUCTIONAL DETAILS OF ELECTRIC APPARATUS; MANUFACTURE OF ASSEMBLAGES OF ELECTRICAL COMPONENTS
    • H05K9/00—Screening of apparatus or components against electric or magnetic fields
    • H05K9/0073—Shielding materials
    • H05K9/0081—Electromagnetic shielding materials, e.g. EMI, RFI shielding
    • H05K9/009—Electromagnetic shielding materials, e.g. EMI, RFI shielding comprising electro-conductive fibres, e.g. metal fibres, carbon fibres, metallised textile fibres, electro-conductive mesh, woven, non-woven mat, fleece, cross-linked
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/005—Continuous casting of metals, i.e. casting in indefinite lengths of wire
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C27/00—Alloys based on rhenium or a refractory metal not mentioned in groups C22C14/00 or C22C16/00
    • C22C27/02—Alloys based on vanadium, niobium, or tantalum
    • C22C27/025—Alloys based on vanadium, niobium, or tantalum alloys based on vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C27/00—Alloys based on rhenium or a refractory metal not mentioned in groups C22C14/00 or C22C16/00
    • C22C27/06—Alloys based on chromium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C45/00—Amorphous alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C45/00—Amorphous alloys
    • C22C45/02—Amorphous alloys with iron as the major constituent
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01C—RESISTORS
    • H01C3/00—Non-adjustable metal resistors made of wire or ribbon, e.g. coiled, woven or formed as grids
    • H01C3/005—Metallic glasses therefor
    • 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
    • H01F1/12—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 soft-magnetic materials
    • H01F1/14—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 soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H01F1/153—Amorphous metallic alloys, e.g. glassy metals
    • H01F1/15391—Elongated structures, e.g. wires

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Microelectronics & Electronic Packaging (AREA)
  • Physics & Mathematics (AREA)
  • Electromagnetism (AREA)
  • Dispersion Chemistry (AREA)
  • Textile Engineering (AREA)
  • Power Engineering (AREA)
  • Soft Magnetic Materials (AREA)
  • Continuous Casting (AREA)
  • Powder Metallurgy (AREA)
  • Materials For Medical Uses (AREA)
  • Surgical Instruments (AREA)
  • Heating, Cooling, Or Curing Plastics Or The Like In General (AREA)
  • Manufacture Of Metal Powder And Suspensions Thereof (AREA)

Description

【発明の詳細な説明】 この発明は新規な非晶質合金に関する。[Detailed description of the invention] This invention relates to a new amorphous alloy.

今迄にもわずかな種類であるが無定形すなわち非晶質ま
たはガラス質合金は製造されてきた。To date, only a few types of amorphous or amorphous or glassy alloys have been produced.

非晶質状態を得るためには、適当な組成を持つ合金溶融
体を急速に冷やすか、あるいは沈着技術を使用しなげれ
ばならない。To obtain the amorphous state, an alloy melt of the appropriate composition must be rapidly cooled or deposition techniques must be used.

蒸着法、スパッタ法、電着または化学（無電気）メッキ
法を適当に用いて非晶質金属を製造できる。Amorphous metals can be produced using suitable methods such as vapor deposition, sputtering, electrodeposition or chemical (electroless) plating.

これら既知技術、すなわち溶融体の急冷法によりあるい
は沈着法により非晶質金属を製造する場合は得られる非
晶質金属の形状は非常に制限される。When producing amorphous metals by these known techniques, ie by quenching of the melt or by deposition methods, the shapes of the amorphous metals obtained are very limited.

例えば非晶質金属を溶融体から得るには、溶融体の急冷
は室温もしくはそれ以下に保ったＣｕまたはＡＩなどの
金属板の上に溶融合金を薄層に広げることにより一般に
行なわれてきた。For example, to obtain amorphous metals from a melt, quenching of the melt has generally been accomplished by spreading the molten alloy in a thin layer onto a metal plate, such as Cu or AI, kept at room temperature or below.

溶融合金を典型的には約０．０５１ｍｍ（０，００２イ
ンチ）の厚さに広げるが（これについての詳細はＲ１Ｐ
ｒｅｄｅｃｋｉ 、 Ａ、Ｗ、 Ｍｕｌｌｅｎｄｏ
ｒｅとＮ、Ｊ。The molten alloy is typically spread to a thickness of about 0.051 mm (0.002 inches) (more information on this can be found in R1P
redecki, A.W., Mullendo.
re and N, J.

ＧｒａｎｔによりＴｒａｎｓ 、 ＡＩＭＥ ２３３
．１５８１（１９６５）に、Ｒ，Ｃ，ＲｕｈｌによりＭ
ａｔ。Trans by Grant, AIME 233
．． 1581 (1965), by R.C. Ruhl, M.
at.

Ｓｃｉ、＆Ｅｎｇ、１．３１３（１９６７）に論じられ
ている。Sci, & Eng, 1.313 (1967).

）、これにより約り０６℃／秒の冷却速度が得られる。), which results in a cooling rate of approximately 06° C./sec.

溶融液体を金属板の上に薄層に広げて急冷を行なう方法
としては多くのものが提案されてきた。Many methods have been proposed for rapidly cooling a molten liquid by spreading it in a thin layer on a metal plate.

これらの方法の代表例としては次のものがある。Representative examples of these methods include:

（１） Ｔｒａｎｓ、 ＡＩＭＥ ２２７．３６２
（１９６３）に記載されているＰ、 Ｄｕｗｅｚ と
ＲｏＨｏＷｉｌｌｅｎｓのガン（ｇｕｎ ）法。(1) Trans, AIME 227.362
(1963), the gun method of P. Duwez and RoHo Willens.

この場合、ガス衝撃波により、銅などの金属板の上に溶
融金属を滴下させる。In this case, a gas shock wave causes molten metal to drip onto a metal plate such as copper.

（２） Ｐ、Ｐｉｅｔｒｏｋｏｗｓｋｙ によりＲ
ｅｖ、 Ｓｃｉ、 Ｉ ｎ５ｔｒ・３４．４４５（１９
６３）に記載されているピストン・アンビル法。(2) P, R by Pietrokowski
ev, Sci, I n5tr・34.445 (19
The piston-anvil method described in 63).

この場合、２枚の金属板を高速でつき合わせ、その隙間
を落下する溶融金属のしずくを平らに伸ばして急冷する
。In this case, two metal plates are brought together at high speed, and the droplets of molten metal that fall through the gap are flattened and rapidly cooled.

（３） Ｒ，Ｐｏｎｄ、 Ｊｒ、 とＲ，Ｍａｄｄ
ｉｎ によりＴｒａｎｓ、 Ｍｅｔ、 Ｓｏｃ 、Ａ
ＩＭＥ ２４５．２４７５（１９６９）に記載されて
いるキャスティング法。(3) R, Pond, Jr. and R, Madd
in Trans, Met, Soc, A
Casting method described in IME 245.2475 (1969).

この場合、溶融金属流を、急速に回転している中空シリ
ンダーの一端の開口部の内表面に衝突させる。In this case, a stream of molten metal impinges on the inner surface of an opening at one end of a rapidly rotating hollow cylinder.

（４） Ｈ，Ｓ、 Ｃｈｅｎ とＣ，ＥｌＭｉｌ
ｌｅｒによりＲｅｙ。(4) H, S, Chen and C, ElMil
Rey by ler.

Ｓ ｃｉ 、 Ｉｎｓｔｒｕｍ、 ４１．１２３７（１
９７０）に記載されている回転ロール法。Sci, Instrum, 41.1237 (1
970).

この場合、溶融金属を高速で回転している一対の金属ロ
ールの間に噴出させる。In this case, molten metal is jetted between a pair of metal rolls rotating at high speed.

急冷法またはメッキ法により最も簡単に非晶質状態にす
ることのできる合金は遷移金属と非金属すなわち半金属
との混合物である。The alloys that can most easily be brought into an amorphous state by quenching or plating are mixtures of transition metals and nonmetals, or metalloids.

岡々の場合これら合金は大体８０原子％の遷移金属と２
０原子％の非金属からなる。In Okaka's case, these alloys contain approximately 80 atomic percent transition metals and 2
Consists of 0 atomic % nonmetal.

非晶質状態にできたと今迄報告されているこのタイプの
合金の実例はＰｄ８４５ｉｔａ、 Ｐｄ７９５ｉ２１
、Ｐｄ７７．５Ｃｕ６Ｓ ｉ１６．５ｖＣＯ８０Ｐ２０
． Ａｕ７６、ｇＧｅ １３．６５ Ｓｌ ｇ、４５、
Ｎ１８ｌ−４Ｐ１３．６、Ｆｅ８０Ｐ１３Ｃ７、Ｎｌ
１５ Ｐｔ ６０Ｐ２５、Ｎｉ４２．５Ｐｄ４２．５Ｐ
Ｉ５． Ｆ’ｅ７５ｐ１５ｃｌＯ。Examples of this type of alloy that have so far been reported to be in an amorphous state are Pd845ita and Pd795i21.
, Pd77.5Cu6S i16.5vCO80P20
．． Au76, gGe 13.65 Sl g, 45,
N18l-4P13.6, Fe80P13C7, Nl
15 Pt 60P25, Ni42.5Pd42.5P
I5. F'e75p15clO.

Ｍｎ７５Ｐ１５Ｃ１０，Ｎｉ３０Ｓ２０そしてＮｉ７８
Ｂ２２（数字は原子％を示す。Mn75P15C10, Ni30S20 and Ni78
B22 (numbers indicate atomic %).

）である。非晶質状態を達成する、すなわち結晶化を避
けるのに必要な冷却速度および一度得た非晶質状態の安
定性は合金の組成に左右される。). The cooling rate required to achieve the amorphous state, ie, avoid crystallization, and the stability of the amorphous state once obtained, depend on the composition of the alloy.

これらの合金の中には他の物より優れたガラス形成体で
あるものがあり、これら“より優れた”合金は比較的低
い冷却速度で非晶質状態を得ることができ（実際上比較
的簡単に得ることができる。Some of these alloys are better glass formers than others, and these "better" alloys can achieve the amorphous state at relatively low cooling rates (in practice, can be obtained easily.

）、あるいは同一方法で溶融体を冷やしても比較的厚い
ものができる。), or even if the molten material is cooled using the same method, a relatively thick material can be obtained.

一般に、非晶質状態を得ることができる既知非晶質組成
物を中心として同様の有用性を持った組成物がわずかで
はあるが存在する。In general, there are a few compositions that have similar usefulness, mainly known amorphous compositions that can obtain an amorphous state.

しかしながら合金を冷却するという技術以外には、一定
の処理条件下で確実に種々多数の合金より非晶質状態が
得られ、それゆえその合金が“より優れた”ガラス形成
体であることを予想できる実用的指針は知られていない
。However, other than the technique of cooling the alloy, one would expect that under certain processing conditions a more amorphous state would be reliably obtained than many different alloys, and that the alloy would therefore be a "better" glass former. There are no known practical guidelines.

非晶質状態と結晶質状態は広範囲の配列規則性の有無に
よりそれぞれ区別される。The amorphous state and the crystalline state are distinguished from each other by the presence or absence of a wide range of sequence regularities.

したがって合金はこれら二つの状態のいずれをとるかに
よりその配列状態が異なる。Therefore, the arrangement state of the alloy differs depending on which of these two states it takes.

この配列の相違はＸ線回折パターンの相違として反映す
る。This difference in arrangement is reflected as a difference in the X-ray diffraction pattern.

それゆえＸ線回折法が結晶質物質を非晶質物質から区別
するのに最も多く使用されている。X-ray diffraction is therefore most often used to distinguish crystalline from amorphous materials.

非晶質物質を回折計で追跡すると回折強度がゆっくりと
変化するのが示され、これは多（の点において液体に似
ており、一方結晶質物質の場合は回折強度がはるかに急
速に変化する。Tracking an amorphous material with a diffractometer shows that the diffraction intensity changes slowly, similar to a liquid in that the diffraction intensity changes much more rapidly, whereas for crystalline materials the diffraction intensity changes much more rapidly. do.

また、原子配置により決まる物理特性は結晶状態と非晶
質状態ではその相違が特に顕著である。Furthermore, the physical properties determined by the atomic arrangement are particularly different between the crystalline state and the amorphous state.

二つの状態では機械的特性は完全に異なっており、例え
ばＰｄ８０Ｓｉ２０の０．０５ｍｍ（０，００２インチ
）厚の非晶質ストリップは比較的高い延性を示しかつ強
靭であり、充分強く曲げた時でも塑性変形するだろうが
、一方、同一組成を持った同様な結晶質ストリップはも
ろくかつ弱（、同一の曲げに対し破砕するだろう。The mechanical properties of the two states are completely different; for example, a 0.05 mm (0,002 inch) thick amorphous strip of Pd80Si20 exhibits relatively high ductility and strength, even when bent sufficiently strongly. will deform plastically, whereas a similar crystalline strip with the same composition will be brittle and weak (and will fracture against the same bending).

更に、二つの状態の磁性および電気特性は異なる。Furthermore, the magnetic and electrical properties of the two states are different.

充分高温に加熱すれば結晶熱の発生と共に準安定状態の
非晶質体は結晶体に転化するだろう。If heated to a sufficiently high temperature, the metastable amorphous substance will convert into a crystalline substance with the generation of heat of crystallization.

更に、溶融金属をガラス状態にまで冷却することと、結
晶状態にまで冷却することとは著しく異なるということ
は心に留めるべきである。Furthermore, it should be kept in mind that cooling molten metal to a glassy state is significantly different from cooling it to a crystalline state.

液体をガラス状態にまで冷却する時は、その液体は溶融
熱を連続的に発生しながらある範囲内の温度で連続的に
固化する。When a liquid is cooled to a glass state, the liquid solidifies continuously at a temperature within a certain range while continuously generating heat of fusion.

対照的に、結晶化は熱力学的−次転移であり、したがっ
て溶融熱および特定の温度と関連づけられる。In contrast, crystallization is a thermodynamic-order transition and is therefore associated with a heat of fusion and a specific temperature.

この発明の一つの目的は、簡単に冷やされ非晶質状態に
なり、高度の安定性を持ち、かつ望ましい物理特性を有
する新規な非晶質合金を提供することである。One object of this invention is to provide a new amorphous alloy that is easily cooled to an amorphous state, has a high degree of stability, and has desirable physical properties.

他の目的および利点は以下の記載および実施例より明ら
かになる。Other objects and advantages will become apparent from the following description and examples.

この発明で興味ある新規組成物はＦｅおよびＮｉから主
として構成される。The novel compositions of interest in this invention are primarily composed of Fe and Ni.

いくつかの組成物すなわちＦｅ７５ＰＩ５Ｃ００、Ｆｅ
８０Ｐ１３Ｃ７、Ｆｅ８０ Ｐ １３ Ｂ７、Ｃ０７３
Ｐ１５Ｂ＋２．Ｆｅ７６ ＢＩ７Ｃ７およびＮｉ７５Ｐ
１ｓＢｉ。Some compositions namely Fe75PI5C00, Fe
80P13C7, Fe80P13B7, C073
P15B+2. Fe76 BI7C7 and Ni75P
1sBi.

はその溶融物から非晶質状態に冷却されたとこれまでに
も報告されている。has previously been reported to have been cooled from its melt to an amorphous state.

しかし、Ｎ１−ＢおよびＦｅ −Ｐ合金については非晶
質になるとの報告はこれまでなかった。However, there has been no report that N1-B and Fe-P alloys become amorphous.

ここに、本発明者らは、合金Ｆｅ３５Ｎｉ４５Ｐ１５Ｂ
６および類似組成な持った合金、例えば Ｆ Ｃ４４Ｎｉ３５ ＰＩ３ Ｂ７ Ｃ１、Ｆ Ｃ４０
Ｎ１４０ ｐ１４ Ｂ６およびＦｅ５（、Ｎｉ５．）Ｐ
、６ Ｂ６が優れたガラス形成性合金であることを発見
した。Here, the inventors have developed an alloy Fe35Ni45P15B
6 and alloys with similar compositions, such as FC44Ni35 PI3 B7 C1, FC40
N140 p14 B6 and Fe5(,Ni5.)P
, 6 B6 was found to be an excellent glass-forming alloy.

炭素は所望により５原子％以下添加される成分である。Carbon is a component that is added in an amount of 5 atomic % or less, if desired.

したがって、本発明者らは、 式： （式中ｄ、ｅ１ｆおよびｇはそれぞれ１５〜５５．３０
〜７０．１０〜２０．１〜１０の原子百分率を表わす。Therefore, the inventors have the following formula: (where d, e1f and g are each 15 to 55.30
~70.10~20.1~10 atomic percentage.

但しｆとｇの和は１５〜２５であり、原子百分率の和は
１００である。However, the sum of f and g is 15 to 25, and the sum of atomic percentages is 100.

）で示され、所望により５原子質分率までの炭素を加え
た非晶質合金によって熱安定性のさらにすぐれたガラス
形成性合金が得られることを見い出した。), and it has been found that glass-forming alloys with even better thermal stability can be obtained by amorphous alloys with optional addition of up to 5 atomic fractions of carbon.

前記組成範囲内にあって本発明に係る合金は通常の冷却
手段で容易に非晶質化が可能である。The alloy according to the present invention within the above composition range can be easily made amorphous by ordinary cooling means.

上に開示した合金は公知のＦ ｅ −Ｎ ｉ −Ｃｏ
ベース合金で可能と思われていた以上に終始一貫して
かつ簡単に非晶質状態に冷却できる。The alloy disclosed above is the known Fe-Ni-Co
It can be cooled to an amorphous state more consistently and easily than was thought possible with base alloys.

そのうえこれら合金はより安定であり、そして加熱に際
しガラス転移を熱的に明示（比熱が突然上昇する）する
が、一方公知のＦｅ −Ｎｉ −Ｃｏ ベース合金は
このようなことはない。Moreover, these alloys are more stable and exhibit thermally a glass transition (sudden increase in specific heat) upon heating, whereas known Fe--Ni--Co based alloys do not.

ガラス転移を熱的に明示する非晶質合金は、明示しない
非晶質合金より簡単に非晶質状態が得られることは普通
である。It is common for amorphous alloys that thermally exhibit a glass transition to attain an amorphous state more easily than amorphous alloys that do not thermally exhibit a glass transition.

この発明の範囲内の組成物は、前記引例に記載されてい
る装置、ポンド（ｐｏｎｄ）＆マシン（Ｍａｄｄｉｎ
）の、あるいはケン（Ｃｈｅｎ ） ＆ミラー （Ｍｉ
ｌｌｅｒ ）の装置、あるいは原理の似ている他の技術
を使ってリボンまたはストリップの形で得ることができ
る。Compositions within the scope of this invention may be applied to the apparatus described in the above reference, the Pond & Machine (Maddin).
) or Ken (Chen) & Miller (Mi
It can be obtained in the form of ribbons or strips using the apparatus of Iller) or other techniques similar in principle.

更に、この発明の溶融金属を例えばシートとして噴出す
る時は類似冷却技術により一層幅広いス） ＩＪツブま
たはシートを得ることができる。Furthermore, when the molten metal of the present invention is ejected as a sheet, for example, a wider range of IJ tubes or sheets can be obtained by similar cooling techniques.

更に、粒径が約０．０１〜０．２５ｍｍ（０，０００４
〜ｏ、ｏｉｏインチ）である、これら非晶質金属の粉末
は、その溶融合金をこのサイズの小滴にし、それからこ
れら小滴を液体（例えば水、冷却塩水、または液体窒素
）中で冷却することにより作ることができる。Furthermore, the particle size is approximately 0.01 to 0.25 mm (0,0004
These amorphous metal powders, which are ~o, oio inches), form the molten alloy into droplets of this size and then cool these droplets in a liquid (e.g., water, chilled brine, or liquid nitrogen). It can be made by

以上論じた合金は高純度要素から作られる。The alloys discussed above are made from high purity elements.

しかしながら、これら合金の利用においてはそれらが、
少量の他元素が溶解している。However, in the use of these alloys, they
Small amounts of other elements are dissolved.

安価な市販材料から作られることが予想される。It is expected that it will be made from inexpensive commercially available materials.

したがってこの発明で考慮されている合金は他元素をわ
ずかに含有してもよく、これら他元素は市販品のＦｅま
たはＮｉ合全中に、例えば原料金属の供給源の結果とし
てかその後の添加中の出来事によりよく発見される。The alloys contemplated in this invention may therefore contain trace amounts of other elements, which may be present during the commercial Fe or Ni synthesis, for example as a result of the source of the raw metal or during subsequent additions. It is often discovered due to the occurrence of

これら元素の実例はＭｏ、Ｔｉ、Ｍｎ、Ｗ、Ｚｒ、Ｈｆ
およびＣｕである。Examples of these elements are Mo, Ti, Mn, W, Zr, Hf
and Cu.

これら非晶質合金は非常に望ましい物理特性を持つ。These amorphous alloys have very desirable physical properties.

例えば、様々な選択された組成物の場合、優れた耐食性
およびユニークな磁性の他に冷却状態で高引張強さ、お
よび高弾性限度を達成できる。For example, for various selected compositions, high tensile strength in the cooled state, and high elastic limits can be achieved in addition to excellent corrosion resistance and unique magnetic properties.

また多くの組成物が非晶質状態で著しく延性であること
が発見されている。It has also been discovered that many compositions are extremely ductile in the amorphous state.

例えばあるものはその厚さより小さい曲率半径をこえて
曲げることができ、ハサミで切ることができる。For example, something can be bent through a radius of curvature smaller than its thickness and can be cut with scissors.

またこれら延性サンプルの場合、約２４６ｋｇ／ｍ４（
３５００００ｐｓｉ）までの引張強さはその冷却状態で
得られた。In addition, in the case of these ductile samples, the weight was approximately 246 kg/m4 (
Tensile strengths of up to 350,000 psi) were obtained in the cooled state.

したがって高引張強さを得るためにしばしば結晶形物質
に与えられる熱処理はこの発明の非晶質金属合金の場合
は省かれる。Therefore, the heat treatment often applied to crystalline materials to obtain high tensile strength is omitted in the case of the amorphous metal alloys of this invention.

この発明は以下の特定実施例により更に詳細に記述され
る。The invention will be described in more detail by the following specific examples.

しかしながら、例えこれら実施例にこの発明の範囲内の
好ましい特定操作変数および割合が詳細に記述されてい
ても、それらは例示目的で与えられているのであり、こ
の発明がそれらに限定されることがないことは理解され
たい。However, even though these examples detail preferred specific operating variables and ratios within the scope of this invention, they are given for illustrative purposes and this invention is not limited thereto. Please understand that there is no such thing.

記載されている部は特記ない限り原子％である。Parts listed are atomic % unless otherwise specified.

実施例 １−４ 成分Ｆｅ、Ｎｉ、Ｐ、ＣおよびＢを生成混合物が第１表
に示す組成となるように量った。Examples 1-4 Components Fe, Ni, P, C and B were weighed so that the resulting mixture had the composition shown in Table 1.

このＦｅ、 Ｎｉ 、 Ｐ、 ＢおよびＣを４５０’Ｃ
（７）、中が空の密閉溶融シリカ管中で１日焼固し、そ
れから真空中１０５０℃で溶融した。This Fe, Ni, P, B and C were heated at 450'C
(7), baked for one day in an empty, closed fused silica tube, and then melted at 1050° C. in vacuo.

この合金を真空中１１００℃で再溶融して最終合金を得
た。This alloy was remelted in vacuo at 1100°C to obtain the final alloy.

これを底に約０．３０５朋（０，０１２インチ）直径の
穴を持つ溶融シリカ管に入れ、１１００℃で溶融した。This was placed in a fused silica tube with an approximately 0.012 inch diameter hole in the bottom and melted at 1100°C.

約０．５６ ｋｇ／ｃｒｒｉ （８ｐｓｉ ）のガス圧
を管にかげ、溶融金属を穴から押し出し、この溶融合金
流を室温に保った、回転している一対のロール中に向け
た。A gas pressure of about 0.56 kg/crri (8 psi) was applied to the tube, forcing the molten metal through the hole and directing the molten metal stream into a pair of rotating rolls maintained at room temperature.

これについてはＣｈｅｎとＭｉｌｌｅｒによりＲｅｖ。
Ｓｃｉ、Ｉｎｓｔｒｕｍ、４１．１２３７（１９７０）
に記載されている。This is revised by Chen and Miller.
Sci, Instrum, 41.1237 (1970)
It is described in.

ロールは共に直径約５０．８ｍｍ（２インチ）であり、
１５０ ｏ ｒｐｍで回転していた。Both rolls are approximately 50.8 mm (2 inches) in diameter;
It was rotating at 150 o rpm.

この冷却金属はＸ線回折測定によると完全に非晶質であ
り、曲げに対し柔軟であった。The cooled metal was completely amorphous and flexible in bending as determined by X-ray diffraction measurements.

Ｆｅ −ｐ−ｃのみを含む合金、例えばＦｅ８０Ｐ１５
Ｃ５、Ｆｅ７７ＰＩ６ｃ７ およびＦｅ７７Ｐ１５Ｃ１
０を同様に冷却したらもろく、かつＸ線回折により調べ
たら部分的に結晶性だった。Alloys containing only Fe-p-c, e.g. Fe80P15
C5, Fe77PI6c7 and Fe77P15C1
When 0 was similarly cooled, it was found to be brittle and partially crystalline when examined by X-ray diffraction.

更にこれらの非晶質合金はガラス転移の熱的明示、すな
わち比熱の急速な上昇を示したが非晶質Ｆｅ −Ｐ−Ｃ
合金は示さなかった。Furthermore, these amorphous alloys showed thermal manifestations of glass transition, i.e., a rapid increase in specific heat, whereas amorphous Fe-P-C
Alloys were not shown.

実施例 ５ 実施例１で得られた非晶質合金 Ｆｅ４ＯＮｉ４０Ｐ１４Ｂ６のガラス遷移温度を測定し
たところ約３９１℃であった。Example 5 The glass transition temperature of the amorphous alloy Fe4ONi40P14B6 obtained in Example 1 was measured and was approximately 391°C.

Claims (1)

【特許請求の範囲】 １ 式： （式中ｄは１５〜５５原千百分率であり、ｅは３０〜７
０原子百分率であり、 ｆは１０〜２０原子百分率であり、 ｇは１〜１０原子百分率である。 但し、ｆとｇの和は１５〜２５原子百分率であり、式中
の原子百分率の和は１００である。 ）で示される組成を有する熱安定性非晶質合金。 ２式： （式中ｄは１５〜５５原子百分率であり、ｅは３０〜７
０原子百分率であり、 ｆは１０〜２０原子百分率であり、 ｇは１〜１０原子百分率であり、 ｈは５原子百分率以下である。 但し、ｆとｇの和は１５〜２５原子百分率であり、式中
の原子百分率の和は１００である。 ）で示される組成を有する熱安定性非晶質合金。[Claims] 1 Formula: (In the formula, d is 15 to 55 original thousand percent, and e is 30 to 7
0 atomic percent, f is 10 to 20 atomic percent, and g is 1 to 10 atomic percent. However, the sum of f and g is 15 to 25 atomic percent, and the sum of the atomic percentages in the formula is 100. ) A thermally stable amorphous alloy having the composition shown in Formula 2: (wherein d is 15 to 55 atomic percent and e is 30 to 7
0 atomic percent, f is 10 to 20 atomic percent, g is 1 to 10 atomic percent, and h is 5 atomic percent or less. However, the sum of f and g is 15 to 25 atomic percent, and the sum of the atomic percentages in the formula is 100. ) A thermally stable amorphous alloy having the composition shown in
JP54163656A 1972-12-26 1979-12-18 amorphous alloy Expired JPS5842256B2 (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
US00318146A US3856513A (en) 1972-12-26 1972-12-26 Novel amorphous metals and amorphous metal articles
US318146306174 1972-12-26

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JPS55107746A JPS55107746A (en) 1980-08-19
JPS5842256B2 true JPS5842256B2 (en) 1983-09-19

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JP53148972A Expired JPS5935417B2 (en) 1972-12-26 1978-12-01 Method for manufacturing amorphous metal wire
JP54163656A Expired JPS5842256B2 (en) 1972-12-26 1979-12-18 amorphous alloy

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JP53148972A Expired JPS5935417B2 (en) 1972-12-26 1978-12-01 Method for manufacturing amorphous metal wire

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JP (3) JPS5519976B2 (en)
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JPS5519976B2 (en) 1980-05-30
IT999851B (en) 1976-03-10
CA1012382A (en) 1977-06-21
JPS4991014A (en) 1974-08-30
DE2366326C2 (en) 1982-10-21
GB1447267A (en) 1976-08-25
JPS55107746A (en) 1980-08-19
DE2364131A1 (en) 1974-06-27
US3856513A (en) 1974-12-24
DE2364131C2 (en) 1990-02-15
FR2211536B1 (en) 1976-06-25
DE2366327C2 (en) 1986-01-02
FR2211536A1 (en) 1974-07-19
JPS5935417B2 (en) 1984-08-28
JPS5499035A (en) 1979-08-04
GB1447268A (en) 1976-08-25

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