JP2000345309A - HIGH STRENGTH AND HIGH CORROSION RESISTANCE Ni BASE AMORPHOUS ALLOY - Google Patents
HIGH STRENGTH AND HIGH CORROSION RESISTANCE Ni BASE AMORPHOUS ALLOYInfo
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、高強度、高耐蝕性
および非晶質形成能に優れたＮｉ基非晶質合金に関する
ものである。The present invention relates to a Ni-based amorphous alloy having high strength, high corrosion resistance and excellent amorphous forming ability.
【０００２】[0002]
【従来の技術】溶融状態の合金を急冷することにより薄
帯状、フィラメント状、粉粒体状等、種々の形状を有す
る非晶質金属材料が得られることはよく知られている。
非晶質合金薄帯は、大きな冷却速度の得られる片ロール
法、双ロール法、回転液中紡糸法等の方法によって容易
に製造できるので、これまでにもＦｅ系、Ｔｉ系、Ｃｏ
系、Ｐｄ系、Ｃｕ系、Ｚｒ系、またはＮｉ系合金につい
て数多くの非晶質合金が得られており、高耐食性、高強
度等の非晶質合金特有の性質が明らかにされている。例
えば、Ｎｉ基非晶質合金としては、Ｎｉ−Ｐｄ−Ｓｉ−
Ｂ−Ａｌ（特開平６−２５８０７号公報）、Ｎｉ−Ｓｉ
−Ｂ（特開平８−２６９６４７公報）、Ｎｉ−Ｐ−Ｂ
（特開平９−１４３６４２公報）などが知られている。2. Description of the Related Art It is well known that an amorphous metal material having various shapes such as a ribbon shape, a filament shape, and a granular material can be obtained by rapidly cooling a molten alloy.
Amorphous alloy ribbons can be easily manufactured by a method such as a single roll method, a twin roll method, or a spinning method in a rotating liquid that can provide a large cooling rate.
Numerous amorphous alloys have been obtained for alloys based on Pd, Pd, Cu, Zr, or Ni, and properties unique to amorphous alloys, such as high corrosion resistance and high strength, have been clarified. For example, Ni-Pd-Si-
B-Al (JP-A-6-25807), Ni-Si
-B (JP-A-8-269647), Ni-P-B
(Japanese Unexamined Patent Application Publication No. 9-143642) and the like are known.
【０００３】しかし、上述した製造方法によって得られ
る非晶質合金は、薄帯やフイラメントに限られており、
それらを用いて最終製品形状へ加工することも困難なこ
とから、工業的にみて、その用途がかなり限定されてい
た。[0003] However, amorphous alloys obtained by the above-described manufacturing method are limited to ribbons and filaments.
Since it is also difficult to process them into a final product shape using them, their use has been considerably limited industrially.
【０００４】従来より報告されている非晶質合金の中に
は、一定の昇温速度で加熱すると結晶化する前に過冷却
液体状態に遷移し、急激な粘性低下を示すものが知られ
ている。例えば、Ｚｒ−Ａ１−Ｎｉ−Ｃｕ非晶質合金で
は毎分４０℃の加熱速度で、結晶化までに約１２０℃程
度の間、過冷却液体領域として存在できると報告されて
いる（「日本金属学会欧文誌」，１９９１年，３２巻，
１００５項参照）。[0004] Among the amorphous alloys that have been reported, when heated at a constant heating rate, they transition to a supercooled liquid state before crystallization and exhibit a sharp drop in viscosity. I have. For example, it has been reported that a Zr-A1-Ni-Cu amorphous alloy can exist as a supercooled liquid region at a heating rate of 40 ° C. per minute and about 120 ° C. before crystallization (“Nippon Metals”). Society of European Literature ”, 1991, 32 volumes,
1005).
【０００５】このような過冷却液体状態では、非晶質合
金の粘性が低下しているために閉塞鍛造等の方法により
任意形状の合金成形体を作製するすることが可能であ
り、非晶質合金からなる歯車なども作製されている
（「日刊工業新聞」，１９９２年，１１月１２日号）。
したがって、広い過冷却液体領域を有する非晶質合金
は、結晶化に対して大きな抵抗力、言い換えれば優れた
非晶質形成能を有するとともに、優れた加工性をも兼備
していると言える。[0005] In such a supercooled liquid state, since the viscosity of the amorphous alloy is reduced, it is possible to produce an alloy compact having an arbitrary shape by a method such as closed forging. Gears and the like made of alloys are also manufactured (“Nikkan Kogyo Shimbun”, November 12, 1992).
Therefore, it can be said that an amorphous alloy having a wide supercooled liquid region has high resistance to crystallization, in other words, excellent amorphous forming ability, and also has excellent workability.
【０００６】一方、本発明と関連するＮｉ基非晶質合金
では、主に磁気的性質（例えば、「Ｓｃｉ．Ｒｅｐ．Ｒ
ＩＴＵ」，１９７９年，Ａ−２７巻，１２７項参照）お
よび耐食性（例えば「Ｓｃｉ．Ｒｅｐ．ＲＩＴＵ」，１
９８０年，Ａ−２８巻，１５６項参照）について着目し
た研究が行われてきた。これらのＮｉ基非晶質合金は、
Ｎｉ−半金属（Ｓｉ，Ｂ，Ｐ，Ｃ）系で示される組成を
有し、主に上述の単ロール法により作製されたリボン状
試料で研究がなされた。しかしながら、実用的な使用を
鑑みた大形状Ｎｉ基非晶質合金、言い換えれば非晶質形
成能に優れたＮｉ基非晶質合金に関する研究開発は進ん
でいない。On the other hand, Ni-based amorphous alloys related to the present invention mainly have magnetic properties (for example, “Sci. Rep. R”).
ITU ", 1979, Vol. A-27, paragraph 127) and corrosion resistance (for example," Sci. Rep. RITU ", 1).
980, A-28, 156). These Ni-based amorphous alloys
Research was conducted on ribbon-shaped samples having a composition indicated by the Ni-metalloid (Si, B, P, C) system and produced mainly by the single roll method described above. However, research and development on large-sized Ni-based amorphous alloys in view of practical use, in other words, Ni-based amorphous alloys having excellent amorphous forming ability, have not been advanced.
【０００７】[0007]
【発明が解決しようとする課題】Ｎｉ系非晶質合金は、
他の非晶質合金に比べて高い結晶化温度を示すため、高
耐熱性を有する新しいタイプの非晶質合金として高強
度、高耐蝕性を要する構造材料、化学材料等の分野への
応用が期待されている。SUMMARY OF THE INVENTION Ni-based amorphous alloys
Since it shows a higher crystallization temperature than other amorphous alloys, it is a new type of amorphous alloy with high heat resistance, and it can be applied to fields such as structural materials and chemical materials that require high strength and high corrosion resistance. Expected.
【０００８】しかしながら、Ｎｉ−半金属系非晶質合金
は、非晶質形成能が小さいために、得られる非晶質合金
形状が薄帯状、フィラメント状、粉粒体状に限られてお
り、一般的な工業材料へ応用できる寸法を有していると
は言えなかった。However, since the Ni-semimetallic amorphous alloy has a small amorphous forming ability, the obtained amorphous alloy shape is limited to a ribbon shape, a filament shape, and a granular material shape. It could not be said that it had dimensions applicable to general industrial materials.
【０００９】[0009]
【課題を解決するための手段】そこで本発明者らは、上
述の課題を解決するために、実用に耐えうる強度と実用
寸法が実現できる非晶質形成能を兼備したＮｉ系非晶質
合金材料を提供することを目的として鋭意研究した結
果、半金属を使用しないでＮｉ基からなる特定組成の合
金を溶融し、液体状態から急冷固化させることにより上
述の性能を具備したＮｉ系非晶質合金が得られることを
見い出し、本発明を完成するに至った。In order to solve the above-mentioned problems, the present inventors have developed a Ni-based amorphous alloy having both the strength to withstand practical use and the ability to form an amorphous form capable of realizing practical dimensions. As a result of diligent research aimed at providing materials, a Ni-based amorphous alloy having the above-mentioned performance was obtained by melting an alloy having a specific composition consisting of Ni base without using a metalloid and rapidly cooling and solidifying it from a liquid state. The inventors have found that an alloy can be obtained, and have completed the present invention.
【００１０】すなわち、本発明は、式：Ｎｉ100-a-b-c
Ｎｂa （Ｚｒ，Ｔｉ，Ｈｆ）b （Ｃｏ，Ｆｅ，Ｃｕ，Ｐ
ｄ）c ［ただし、式中のａ〜ｃは、原子比率であり、そ
れぞれａ＝１０〜２８，ｂ＝１０〜２８，ｃ＝０〜１
５，ａ＋ｂ＝３５〜４２，ａ＋ｂ＋ｃ＝３５〜５０であ
り、残部はＮｉおよび不可避的不純物から構成される］
で示される組成を有し、３０Ｋ以上の過冷却液体領域と
８００Ｋ以上のガラス遷移温度を兼備した、非晶質相を
体積百分率で５０％以上含む高強度・高耐蝕性Ｎｉ基非
晶質合金を提供するものである。That is, the present invention relates to a compound represented by the formula: Ni 100-abc
Nb a (Zr, Ti, Hf ) b (Co, Fe, Cu, P
d) c [where a to c in the formula are atomic ratios, and a = 10 to 28, b = 10 to 28, c = 0 to 1 respectively.
5, a + b = 35 to 42, a + b + c = 35 to 50, and the balance is composed of Ni and unavoidable impurities]
A high-strength and high-corrosion-resistant Ni-based amorphous alloy containing a supercooled liquid region of 30K or more and a glass transition temperature of 800K or more and containing an amorphous phase of 50% or more by volume. Is provided.
【００１１】なお、本明細書中の「過冷却液体領域」と
は、毎分４０℃の加熱速度で示差走査熱量分析を行うこ
とにより得られるガラス遷移温度と結晶化温度の差で定
義される。「過冷却液体領域」の値は、加工性を示す数
値である。The "supercooled liquid region" in this specification is defined as a difference between a glass transition temperature and a crystallization temperature obtained by performing differential scanning calorimetry at a heating rate of 40 ° C. per minute. . The value of the “supercooled liquid region” is a numerical value indicating workability.
【００１２】上述の過冷却液体領域の規定で示される値
により、本発明のＮｉ基非晶質合金は、公知のＮｉ基非
晶質合金に比べて大幅に非晶質形成能が改善されている
ことが分かる。このため、公知のＮｉ基非晶質合金では
実現できなかった塊状試料の製造が可能となる。According to the value specified in the above-mentioned definition of the supercooled liquid region, the Ni-based amorphous alloy of the present invention has significantly improved amorphous forming ability as compared with the known Ni-based amorphous alloy. You can see that there is. For this reason, it becomes possible to manufacture a massive sample that cannot be realized by a known Ni-based amorphous alloy.
【００１３】本発明で規定する合金の組成範囲において
は、０．５ｍｍ2以上の断面積、例えば、金型鋳造法に
より直径１ｍｍ（０．７８５ｍｍ2の断面積）の線状の
非晶質合金塊が容易に得られる。この合金塊を用いる
と、公知のＮｉ基非晶質合金では測定が不可能であった
塊状試料での機械的性質の測定が可能となる。In the composition range of the alloy specified in the present invention, a linear amorphous alloy having a cross-sectional area of 0.5 mm 2 or more, for example, a diameter of 1 mm (a cross-sectional area of 0.785 mm 2 ) by die casting is used. Lumps are easily obtained. The use of this alloy lump makes it possible to measure the mechanical properties of a lump sample, which cannot be measured with a known Ni-based amorphous alloy.
【００１４】金属元素より構成される合金は、非晶質化
することにより一般にその機械的性質が向上するが、本
発明のＮｉ基非晶質合金においては、塊状試料で容易に
２，５００ＭＰａを超える圧縮強度を持ったものが容易
に得られた。このため、本発明のＮｉ基非晶質合金から
製造される塊状試料を実施態様として請求項２におい
て、具体的に断面積を０．５ｍｍ2 以上、圧縮強度を
２，５００ＭＰａ以上と規定した。なお、リボン材の引
張強度は圧縮強度と同程度である。An alloy composed of a metal element is generally improved in mechanical properties by being made amorphous. However, in the case of the Ni-based amorphous alloy of the present invention, 2,500 MPa is easily applied to a bulk sample. A material having a compressive strength exceeding the above was easily obtained. For this reason, a block sample produced from the Ni-based amorphous alloy of the present invention is specified in claim 2 as an embodiment. Specifically, the sectional area is specified to be 0.5 mm 2 or more and the compressive strength is specified to be 2,500 MPa or more. Note that the tensile strength of the ribbon material is almost equal to the compressive strength.
【００１５】本発明の合金は、強度と耐摩耗性が要求さ
れる小型精密機器の部品および耐蝕性が要求される配管
等に適する特性を有している。The alloy of the present invention has characteristics suitable for parts of small precision equipment which requires strength and wear resistance, and pipes which require corrosion resistance.
【００１６】[0016]
【発明の実施の形態】以下に本発明の実施の形態を説明
する。本発明のＮｉ基非晶質合金において、Ｎｂ（ニオ
ブ）は、非晶質を形成する基本となる元素である。Ｎｂ
は、１０原子％以上２８原子％以下で、好ましくは１５
原子％以上２５原子％以下である。Embodiments of the present invention will be described below. In the Ni-based amorphous alloy of the present invention, Nb (niobium) is a basic element for forming an amorphous. Nb
Is at least 10 atomic% and at most 28 atomic%, preferably at least 15 atomic%.
It is at least 25 atomic%.
【００１７】また、Ｚｒ、Ｔｉ、Ｈｆよりなる群から選
択される１種または２種以上の元素は、本発明の合金の
基幹となる元素群で、Ｎｉ−Ｎｂ系合金の非晶質形成能
を大幅に高める効果を有する。この元素群の含有量が１
０原子％未満では、非晶質形成能の向上は認められな
い。また、２８原子％以上では冷却速度の大きな片ロー
ル法によっても非晶質相は形成されなくなる。One or more elements selected from the group consisting of Zr, Ti, and Hf are the basic elements of the alloy of the present invention, and are capable of forming an amorphous Ni-Nb alloy. Has the effect of significantly increasing the When the content of this element group is 1
At less than 0 atomic%, no improvement in the ability to form an amorphous phase is observed. If it is 28 atomic% or more, no amorphous phase is formed even by the single roll method with a high cooling rate.
【００１８】非晶質相の形成上は、ＮｂおよびＺｒ、Ｔ
ｉ、またはＨｆの元素群の合計量は、好ましくは、３５
原子％以上４２原子％以下であり、４２原子％超では３
０Ｋ以上の過冷却液体領域を示さないため、加工性が劣
化する。したがって、本発明では、ＮｂおよびＺｒ、Ｔ
ｉ、Ｈｆよりなる群から選択される１種または２種以上
の元素の合計含有量を３５原子％以上４２原子％以下と
規定した。In order to form the amorphous phase, Nb and Zr, T
The total amount of the element group of i or Hf is preferably 35
At least 42 atomic%, and over 42 atomic%, 3
Since no supercooled liquid region of 0K or more is exhibited, workability is deteriorated. Therefore, in the present invention, Nb and Zr, T
The total content of one or two or more elements selected from the group consisting of i and Hf was specified to be from 35 at% to 42 at%.
【００１９】Ｎｉは、１５原子％まではＣｏ，Ｆｅ，Ｃ
ｕ，Ｐｄによって置換しても過冷却液体領域の広さは、
ほとんど変わらず３０〜７０Ｋであるが、１５原子％を
超えると過冷却液体領域が３０Ｋ未満となり、非晶質形
成能が低下する。Ni is Co, Fe, C up to 15 atomic%.
The size of the supercooled liquid region is equal to
It is 30-70K almost unchanged, but if it exceeds 15 atomic%, the supercooled liquid region becomes less than 30K, and the ability to form an amorphous is reduced.
【００２０】本発明のＮｉ基非晶質合金は、公知のＮｉ
系非晶質合金と同様、溶融状態から公知の片ロール法、
双ロール法、回転液中紡糸法、アトマイズ法等の種々の
方法で冷却固化させ、薄帯状、フィラメント状、粉粒体
状の非晶質固体を得ることができる。また、本発明のＮ
ｉ基非晶質合金は、公知のＮｉ基非晶質合金に比べて大
幅に非晶質形成能が改善されているため、上述の公知の
製造方法のみならず、好ましくは、溶融合金を金型に充
填鋳造することにより任意の形状の非晶質合金を得るこ
ともできる。The Ni-based amorphous alloy according to the present invention can
Known single-roll method from the molten state,
It can be cooled and solidified by various methods such as a twin-roll method, a spinning in a rotating liquid method, an atomizing method, and the like, to obtain a ribbon-like, filament-like, or granular amorphous solid. In addition, N of the present invention
Since the i-based amorphous alloy has significantly improved amorphous forming ability as compared with the known Ni-based amorphous alloy, not only the above-described known manufacturing method but also preferably the molten alloy is made of gold. An amorphous alloy of any shape can be obtained by filling and casting in a mold.
【００２１】例えば、代表的な金型鋳造法においては、
合金を石英管中でアルゴン雰囲気中で溶融した後、溶融
合金を噴出圧０．５〜３．０ｋｇ／ｃｍ2 で銅製の金型
内に充填凝固させることにより非晶質合金塊を得ること
ができる。さらには、アーク溶解法、石英管水焼き入れ
法、ダイカストキャスティング法およびスクイズキャス
ティング法等の製造方法を適宜用いることもできる。For example, in a typical mold casting method,
After melting the alloy in a quartz tube in an argon atmosphere, the molten alloy is filled and solidified in a copper mold at an ejection pressure of 0.5 to 3.0 kg / cm 2 to obtain an amorphous alloy mass. it can. Further, manufacturing methods such as an arc melting method, a quartz tube water quenching method, a die casting method, and a squeeze casting method can be used as appropriate.
【００２２】[0022]
【実施例】以下、本発明の実施例について説明する。表
１に示す合金組成からなる材料（実施例１〜２１、比較
例１〜５）の薄帯状合金塊試料および直径１ｍｍの線状
の合金塊試料を、片ロール法および金型鋳造法により作
製した。薄帯状合金塊試料のガラス遷移温度（Ｔｇ）、
結晶化開始温度（Ｔｘ）を示差走査熱量分析により測定
した。Embodiments of the present invention will be described below. A strip-shaped alloy lump sample and a linear alloy lump sample having a diameter of 1 mm of materials (Examples 1 to 21 and Comparative Examples 1 to 5) having the alloy compositions shown in Table 1 were produced by a single roll method and a die casting method. did. Glass transition temperature (Tg) of the ribbon-shaped alloy ingot sample,
The crystallization onset temperature (Tx) was measured by differential scanning calorimetry.
【００２３】これらの値より過冷却液体領域（Ｔｘ−Ｔ
ｇ）Ｋを算出した。また、金型鋳造法により作製した直
径１ｍｍの線状の合金塊の非晶質化の確認をＸ線回折法
および試料断面の光学顕微鏡観察により行った。また、
試料中に含まれる非晶質相の体積分率（Ｖｆ−ａｍｏ）
は、示差走査熱量分析を用いて、結晶化の際の発熱量を
完全非晶質化した片ロール箔帯との比較により評価し
た。さらに、圧縮試験片を機械加工により作製し、イン
ストロン型試験機を用いた圧縮試験により破断強度（σ
ｆ）を評価した。これらの結果を表１に示す。From these values, the supercooled liquid region (Tx-T
g) K was calculated. In addition, the confirmation of the amorphization of the linear alloy lump having a diameter of 1 mm produced by the die casting method was confirmed by an X-ray diffraction method and an optical microscope observation of a cross section of the sample. Also,
Volume fraction of amorphous phase contained in the sample (Vf-amo)
Was evaluated by using differential scanning calorimetry for the calorific value during crystallization by comparison with a single roll foil band that was completely amorphized. Further, a compression test piece was prepared by machining, and a breaking test (σ) was performed by a compression test using an Instron type testing machine.
f) was evaluated. Table 1 shows the results.
【００２４】[0024]
【表１】 [Table 1]
【００２５】また、図１〜３は、実施例２、４、１５の
合金を大気中で２９３Ｋの１Ｍ塩酸溶液中で測定したＮ
ｉ基非晶質合金の定電位分極曲線である。表１より明ら
かなように、実施例１〜２１の非晶質合金は、３０Ｋ以
上の過冷却液体領域を示すとともに、直径１ｍｍの線状
の非晶質合金塊においても２，５００ＭＰａを超える圧
縮強度を示す。また、図１〜３に示すように、各実施例
の非晶質合金は、１Ｍ塩酸溶液中でいずれも不働態化し
ている。また、約１５００ｍＶの高電位まで分極しても
孔食が発生しない優れた耐食性を有していることが明ら
かである。FIGS. 1 to 3 show the N, N and N alloys measured in the 293 K 1M hydrochloric acid solution in the air.
It is a constant potential polarization curve of an i-base amorphous alloy. As is clear from Table 1, the amorphous alloys of Examples 1 to 21 show a supercooled liquid region of 30K or more and have a compression of more than 2,500 MPa even in a linear amorphous alloy lump having a diameter of 1 mm. Indicates strength. Further, as shown in FIGS. 1 to 3, the amorphous alloys of the respective examples were all passivated in a 1M hydrochloric acid solution. It is also apparent that the material has excellent corrosion resistance in which pitting does not occur even when polarized to a high potential of about 1500 mV.
【００２６】これらの実施例に対し、比較例１の合金
は、Ｚｒが２８原子％を超え、冷却速度の大きな片ロー
ル法によっても非晶質相は形成されなくなり、直径１ｍ
ｍの線状の非晶質合金塊が得られず、圧縮強度の測定は
不能であった。In contrast to these examples, the alloy of Comparative Example 1 has a Zr of more than 28 atomic%, an amorphous phase is not formed even by a single roll method with a high cooling rate, and a diameter of 1 m
m was not obtained, and it was impossible to measure the compressive strength.
【００２７】比較例２の合金は、ＮｂおよびＺｒが本発
明で規定する含有量の範囲を満たさないために、片ロー
ル法により作製したリボンでは非晶質化するものの、金
型鋳造法では非晶質相を体積分率で５０％以上含む非晶
質合金塊が得られない。このため、直径１ｍｍの線状の
合金塊試料では結晶化したために脆く、圧縮強度が小さ
い。したがって、実用に耐えうる機械的性質を有してい
ないといえる。In the alloy of Comparative Example 2, since Nb and Zr do not satisfy the content range specified in the present invention, the ribbon produced by the single roll method is amorphized, but is not formed by the die casting method. An amorphous alloy lump containing a crystalline phase in a volume fraction of 50% or more cannot be obtained. For this reason, a linear alloy lump sample having a diameter of 1 mm is brittle due to crystallization and has low compressive strength. Therefore, it can be said that it does not have mechanical properties that can withstand practical use.
【００２８】比較例３の合金は、ＮｂおよびＴｉ元素を
本発明で規定する含有量にて含むものの、含有量の合計
が４２原子％を超え、冷却速度の大きな片ロール法によ
り作製したリボンでは非晶質化するが、直径１ｍｍの線
状の非晶質合金塊が得られず、圧縮強度の測定は不能で
あった。Although the alloy of Comparative Example 3 contains the elements Nb and Ti at the contents specified in the present invention, the total of the contents exceeds 42 at% and the ribbon produced by the single roll method with a large cooling rate is not used. Although it became amorphous, a linear amorphous alloy lump having a diameter of 1 mm was not obtained, and it was impossible to measure the compressive strength.
【００２９】比較例４および比較例５の合金は、Ｎｂお
よびＴｉ元素を本発明で規定する含有量にて含むもの
の、含有量の合計が４２原子％を超え、冷却速度の大き
な片ロール法によっても非晶質化せず、直径１ｍｍの線
状の合金塊試料は結晶化したために脆く、圧縮試験がで
きず、圧縮強度の測定は不能であった。The alloys of Comparative Examples 4 and 5 contain the elements Nb and Ti at the contents specified in the present invention, but the total content exceeds 42 at% and the single-roll method with a large cooling rate is used. However, the linear alloy lump sample having a diameter of 1 mm was also brittle because it was crystallized, so that a compression test could not be performed, and the measurement of compressive strength was impossible.
【００３０】[0030]
【発明の効果】以上説明したように、本発明のＮｉ基非
晶質合金は、３０Ｋ以上の過冷却液体領域を示すととも
に、０．５ｍｍ2 以上の断面積の非晶質合金塊において
も２，５００ＭＰａを超える圧縮強度を示す。これらの
要件を備えることにより本発明は、ガラス形成能、加工
性、機械的強度、耐摩耗性等に優れたＮｉ系非晶質合金
を提供することができるものである。As described above, the Ni-based amorphous alloy of the present invention exhibits a supercooled liquid region of 30 K or more, and has a small cross-sectional area of 0.5 mm 2 or more. , Exhibiting a compressive strength exceeding 500 MPa. By satisfying these requirements, the present invention can provide a Ni-based amorphous alloy excellent in glass forming ability, workability, mechanical strength, abrasion resistance and the like.
【図１】実施例２の定電位分極曲線を示すグラフ。FIG. 1 is a graph showing a constant potential polarization curve of Example 2.
【図２】実施例４の定電位分極曲線を示グラフ。FIG. 2 is a graph showing a constant potential polarization curve of Example 4.
【図３】実施例１５の定電位分極曲線を示すグラフ。FIG. 3 is a graph showing a constant potential polarization curve of Example 15.
Claims (2)
ｉ，Ｈｆ）b （Ｃｏ，Ｆｅ，Ｃｕ，Ｐｄ）c ［ただし、
式中のａ〜ｃは、原子比率であり、それぞれａ＝１０〜
２８，ｂ＝１０〜２８，ｃ＝０〜１５，ａ＋ｂ＝３５〜
４２，ａ＋ｂ＋ｃ＝３５〜５０であり、残部はＮｉおよ
び不可避的不純物から構成される］で示される組成を有
し、３０Ｋ以上の過冷却液体領域と８００Ｋ以上のガラ
ス遷移温度を兼備した、非晶質相を体積百分率で５０％
以上含む高強度・高耐蝕性Ｎｉ基非晶質合金。1. A formula: Ni 100-abc Nb a ( Zr, T
i, Hf) b (Co, Fe, Cu, Pd) c [where
A to c in the formula are atomic ratios, and a = 10 to 10 respectively.
28, b = 10 to 28, c = 0 to 15, a + b = 35 to
42, a + b + c = 35 to 50, with the balance being composed of Ni and unavoidable impurities], and having both a supercooled liquid region of 30 K or more and a glass transition temperature of 800 K or more. 50% by volume percentage of mass phase
A high-strength, high-corrosion-resistant Ni-based amorphous alloy including the above.
ＭＰａ以上の圧縮強度を有する請求項１記載の高強度・
高耐蝕性および非晶質形成能に優れたＮｉ基非晶質合金
塊。 2. A cross-sectional area of 0.5 mm 2 or more and 2,500
The high strength according to claim 1, which has a compressive strength of not less than MPa.
Ni-based amorphous alloy ingot with high corrosion resistance and excellent amorphous forming ability.
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| JP16304599A JP3880245B2 (en) | 1999-06-09 | 1999-06-09 | High strength and high corrosion resistance Ni-based amorphous alloy |
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2005024274A1 (en) | 2003-09-02 | 2005-03-17 | Namiki Seimitsu Houseki Kabushiki Kaisha | Precision gear, its gear mechanism and production method of precision gear |
| WO2007029906A1 (en) * | 2005-09-09 | 2007-03-15 | Korea Institute Of Science And Technology | Amorphous alloy and manufacturing method thereof |
| CN100429329C (en) * | 2007-02-09 | 2008-10-29 | 浙江大学 | Ni-Nb-Zr-Co bulk amorphous alloy |
| CN100453687C (en) * | 2005-12-14 | 2009-01-21 | 中国科学院物理研究所 | Nickle-based block metal glass and its production |
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|---|---|---|---|---|
| CN103834878B (en) * | 2014-03-25 | 2016-03-09 | 北京航空航天大学 | A kind of Cr containing Cr amA bmB cmC dnon-crystaline amorphous metal |
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1999
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Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2005024274A1 (en) | 2003-09-02 | 2005-03-17 | Namiki Seimitsu Houseki Kabushiki Kaisha | Precision gear, its gear mechanism and production method of precision gear |
| JPWO2005024274A1 (en) * | 2003-09-02 | 2006-11-30 | 並木精密宝石株式会社 | Precision gear, its gear mechanism, and method of manufacturing precision gear |
| CN101929537A (en) * | 2003-09-02 | 2010-12-29 | 并木精密宝石株式会社 | Precision gear and production method of precision gear |
| JP4801800B2 (en) * | 2003-09-02 | 2011-10-26 | 並木精密宝石株式会社 | Precision gear, its gear mechanism, and method of manufacturing precision gear |
| KR101363145B1 (en) | 2003-09-02 | 2014-02-13 | 나미키 세이미쓰 하우세키 가부시키가이샤 | Precision gear, its gear mechanism and production method of precision gear |
| WO2007029906A1 (en) * | 2005-09-09 | 2007-03-15 | Korea Institute Of Science And Technology | Amorphous alloy and manufacturing method thereof |
| US8070891B2 (en) | 2005-09-09 | 2011-12-06 | Korea Institute Of Science And Technology | Amorphous alloy and manufacturing method thereof |
| US20120024431A1 (en) * | 2005-09-09 | 2012-02-02 | Korea Institute Of Science And Technology | Amorphous alloy |
| CN100453687C (en) * | 2005-12-14 | 2009-01-21 | 中国科学院物理研究所 | Nickle-based block metal glass and its production |
| CN100429329C (en) * | 2007-02-09 | 2008-10-29 | 浙江大学 | Ni-Nb-Zr-Co bulk amorphous alloy |
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