JPS5891144A - Amorphous metal alloy having high crystalline temperature and high hardness - Google Patents
Amorphous metal alloy having high crystalline temperature and high hardnessInfo
- Publication number
- JPS5891144A JPS5891144A JP19070082A JP19070082A JPS5891144A JP S5891144 A JPS5891144 A JP S5891144A JP 19070082 A JP19070082 A JP 19070082A JP 19070082 A JP19070082 A JP 19070082A JP S5891144 A JPS5891144 A JP S5891144A
- Authority
- JP
- Japan
- Prior art keywords
- atoms
- range
- hardness
- metal
- amorphous
- 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 description 5
- 238000002425 crystallisation Methods 0.000 claims description 15
- 230000008025 crystallization Effects 0.000 claims description 15
- 239000010955 niobium Substances 0.000 claims description 7
- 239000010936 titanium Substances 0.000 claims description 6
- 229910052758 niobium Inorganic materials 0.000 claims description 5
- 229910052719 titanium Inorganic materials 0.000 claims description 5
- 229910052721 tungsten Inorganic materials 0.000 claims description 5
- 229910052726 zirconium Inorganic materials 0.000 claims description 4
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 3
- 229910052715 tantalum Inorganic materials 0.000 claims description 3
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 claims description 3
- 239000010937 tungsten Substances 0.000 claims description 3
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 2
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 claims description 2
- GUVRBAGPIYLISA-UHFFFAOYSA-N tantalum atom Chemical compound [Ta] GUVRBAGPIYLISA-UHFFFAOYSA-N 0.000 claims description 2
- 229910052751 metal Inorganic materials 0.000 description 21
- 239000002184 metal Substances 0.000 description 21
- 239000000203 mixture Substances 0.000 description 16
- 229910045601 alloy Inorganic materials 0.000 description 14
- 239000000956 alloy Substances 0.000 description 14
- 239000005300 metallic glass Substances 0.000 description 7
- 150000002739 metals Chemical class 0.000 description 7
- 238000001816 cooling Methods 0.000 description 6
- 239000000463 material Substances 0.000 description 6
- 238000002844 melting Methods 0.000 description 6
- 230000008018 melting Effects 0.000 description 6
- 238000010791 quenching Methods 0.000 description 6
- 239000011888 foil Substances 0.000 description 5
- 238000000034 method Methods 0.000 description 5
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 3
- 229910052802 copper Inorganic materials 0.000 description 3
- 239000010949 copper Substances 0.000 description 3
- 229910003460 diamond Inorganic materials 0.000 description 3
- 239000010432 diamond Substances 0.000 description 3
- 239000011521 glass Substances 0.000 description 3
- 238000007496 glass forming Methods 0.000 description 3
- 230000000171 quenching effect Effects 0.000 description 3
- 238000002441 X-ray diffraction Methods 0.000 description 2
- 238000007792 addition Methods 0.000 description 2
- 229910002056 binary alloy Inorganic materials 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 238000010891 electric arc Methods 0.000 description 2
- 230000009477 glass transition Effects 0.000 description 2
- 239000007788 liquid Substances 0.000 description 2
- 239000000155 melt Substances 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 239000000758 substrate Substances 0.000 description 2
- 235000002492 Rungia klossii Nutrition 0.000 description 1
- 244000117054 Rungia klossii Species 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 229910004154 TaNi Inorganic materials 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 239000004035 construction material Substances 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000004455 differential thermal analysis Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000002003 electron diffraction Methods 0.000 description 1
- 230000001747 exhibiting effect Effects 0.000 description 1
- 239000005357 flat glass Substances 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 239000000843 powder Substances 0.000 description 1
- 238000002407 reforming Methods 0.000 description 1
- 239000003870 refractory metal Substances 0.000 description 1
- 239000012783 reinforcing fiber Substances 0.000 description 1
- 238000012552 review Methods 0.000 description 1
- 230000035939 shock Effects 0.000 description 1
- 238000005245 sintering Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 239000010935 stainless steel Substances 0.000 description 1
- 229910001220 stainless steel Inorganic materials 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 238000004627 transmission electron microscopy Methods 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C45/00—Amorphous alloys
- C22C45/10—Amorphous alloys with molybdenum, tungsten, niobium, tantalum, titanium, or zirconium or Hf as the major constituent
Abstract
(57)【要約】本公報は電子出願前の出願データであるた
め要約のデータは記録されません。(57) [Summary] This bulletin contains application data before electronic filing, so abstract data is not recorded.
Description
【発明の詳細な説明】
本発明は非晶質金属合金組成物、特に実質量の元素Ｔａ
、Ｎｂ及びＷの−又はそれ以上を含む組成物に関し、こ
れは高い結晶化温度、高い硬■値の両方を示ｆ０
研究によれば成る種の合金組成物につい人固体非晶質金
ｍを得ることの可能であることが示されており、ここに
用語「非晶質」とは「固体の非晶質」を意味する。非晶
質物質は一般に非結晶質またはガラス質物質を特徴とす
る。即ちその物質は実質的に何らの長範囲の秩序を持た
ない。非晶質物質と結晶質物質との区別では一般ＫＸ線
回折測定を使うのが適当である。更に透過電子顕微鏡写
真法および電子回折を非晶質および結晶状態の区別に使
うことができる。DETAILED DESCRIPTION OF THE INVENTION The present invention provides amorphous metal alloy compositions, particularly those containing a substantial amount of the element Ta.
, Nb and W, which exhibit both high crystallization temperatures and high hardness values. The term "amorphous" herein means "solid amorphous". Amorphous materials are generally characterized as non-crystalline or glassy materials. That is, the material has virtually no long-range order. It is appropriate to use general KX-ray diffraction measurement to distinguish between amorphous substances and crystalline substances. Furthermore, transmission electron microscopy and electron diffraction can be used to distinguish between amorphous and crystalline states.
非晶質金属はＸ線回折像でその強さが回折角と共にゆる
やかに変る。この様な像は液体や通常の窓ガラスの回折
像に定性的に類似している。一方結晶質金属では回折像
の強さが回折角と共に急速に変る。In X-ray diffraction images of amorphous metals, the intensity changes gradually with the diffraction angle. Such an image is qualitatively similar to the diffraction image of a liquid or an ordinary window glass. On the other hand, in crystalline metals, the intensity of the diffraction pattern changes rapidly with the diffraction angle.
これらの非晶質金属は準安定状態にある。充分高温度に
加熱するとそれは結晶化熱の発生と共に結晶化し、そし
て回折像はガラス状または非晶質特性をもつものから結
晶質特性をもつものへ変る。These amorphous metals are in a metastable state. When heated to a sufficiently high temperature, it crystallizes with the generation of heat of crystallization, and the diffraction pattern changes from having a glassy or amorphous character to having a crystalline character.
非晶質および結晶質の二相混合物である金属を造ること
は可能であり、その相対割合は全部結晶質のものから全
部非晶質のものへ変り得る。ここで使う様な非晶質金属
とは、王として非晶質である金属をいう、即ち少（とも
５０４が非晶質であって然し介在するりｌ＋スタリット
として存在する少部分の材料をもってもよい。It is possible to create metals that are two-phase mixtures of amorphous and crystalline, the relative proportions of which can vary from fully crystalline to fully amorphous. As used herein, an amorphous metal refers to a metal that is primarily amorphous, i.e., even if at least 504 is amorphous but has a small amount of material present as intervening or starite. good.
適当な組成物に対しては適当な処理で非晶質状態の金属
を生じるだろう。一つの代表的な操゛作は溶融合金な銅
ま１こはアルミニウムの様な固体金属基質と接触させて
薄く拡がらせて溶融金属の熱を急速に基質の方に失わせ
ることである。For appropriate compositions, appropriate processing will yield the metal in an amorphous state. One typical operation is to spread a thin layer of molten alloy copper in contact with a solid metal substrate, such as aluminum, so that the heat of the molten metal is rapidly lost to the substrate.
合金が厚さ約０．００２インチに拡げられると１０６℃
／秒程度の冷却速度が達成されるであろう。106°C when the alloy is expanded to a thickness of about 0.002 inches
Cooling rates on the order of 1/sec may be achieved.
ｆｌｌｌｌエバＣ，ルール（マチＩＩアルズーサイエン
ス・アントゞ・エンジニア１１ング、第１巻、５１．５
−６１９ページ、１９６７年）が冷却速度の溶融金属の
処理条件への依存性を論じているのを参照されたい。適
当な組成の合金に対しかつ充分高い冷却速度に対しては
この様な処理が＝４ｋ１４金属を生じる。適当な高冷却
速度を与える任意の方法を使うことができる。非晶質金
属を造るのに使える操作の例示的な例にはＨ，Ｓ、チャ
ン及びＣ，Ｅ、 ミラー（レビュー・オブ・サイエンテ
ィフィク・インストルメンツ、１２＋７−１２６８ペー
ジ、１９７０年）が書いている様な回転二重ローラー、
Ｒ，ボンド・ジュニア及びＲ，マデイン（トランザクシ
ョンズ・オブ・ザ・メタルΦソサイエテイ’、ＡＩＭＥ
。fllll Eva C, Rule (Machi II Arzu Science Antozu Engineer 11ng, Volume 1, 51.5
-619, 1967) discussing the dependence of the cooling rate on the processing conditions of the molten metal. For alloys of appropriate composition and for sufficiently high cooling rates, such treatment yields =4k14 metal. Any method that provides a suitably high cooling rate can be used. Illustrative examples of operations that can be used to create amorphous metals include those written by H.S., Chan and C.E., Miller (Review of Scientific Instruments, pp. 12+7-1268, 1970). Rotating double rollers,
R. Bond Jr. and R. Madeline (Transactions of the Metal Φ Society', AIME
.
第２４５巻、２４７５−２４７６ページ、１９６９年）
が書いている様な回転円柱法がある。Volume 245, pages 2475-2476, 1969)
There is a rotating cylinder method as described by.
実質型のＦｅ、ＮＬＣｏ、Ｖ及びＣｒ元素の１またはそ
れ以上を含む琲晶暎合金がＨ，Ｓ、チャンとＣ，Ｅ。Crystal alloys containing one or more of the elements Fe, NLCo, V and Cr in substantial form include H, S, Chang, C, and E.
ミラーの１９７２年１２月２６日付米国特許出願第５１
８．１４６号に記載されている。この様な合金は種々の
用途に対し全く有用である。然しこの様な合金は約４２
５″〜５５０℃の結晶化温度および約６００〜７５０Ｄ
ＰＨ（ダイヤモンド゛角錐硬度）の硬度により特徴づけ
られる。Miller, U.S. Patent Application No. 51, dated December 26, 1972
8.146. Such alloys are extremely useful for a variety of applications. However, such an alloy is about 42
Crystallization temperature of 5″~550℃ and about 600~750D
It is characterized by the hardness of PH (diamond pyramid hardness).
本発明によれば、約６５０°〜９７５℃の範囲の結晶化
温度の高い熱安定性と、約８００〜１４００Ｄ Ｐ Ｈ
の範囲の値の高い硬度とをもつ非晶質合金が記載される
。下記の一般的組ｆｉ！を有する合金がこれらの性質ケ
有している。According to the present invention, high thermal stability with crystallization temperatures ranging from about 650° to 975°C and about 800 to 1400 D P H
Amorphous alloys with high hardness values in the range are described. General group fi below! Alloys with these properties have these properties.
すなわち金属−令属系と呼ぶことのできる、一般式Ｒｒ
Ｎ ｉｇＴ ｔまたはＲｒＮｉ、で表わされる組成を有
する耐火性金属基礎のガラス質金属である。式中Ｒは元
素タンタル、ニオブ及びタングステンの少（も一つであ
り、Ｔは元素チタン及びジルコニウムの少（とも一つで
あり、そしてｒは６５〜６５原子鴫の範囲にあり、Ｓは
２５〜６５原子唾の範囲ｆあり、ｔは１５原子４以下の
範囲にある。In other words, the general formula Rr can be called a metal-order system.
It is a refractory metal-based glassy metal with a composition represented by N igT t or RrNi. where R is one of the elements tantalum, niobium and tungsten; T is one of the elements titanium and zirconium; and r is in the range of 65 to 65 atoms; S is 25 There is a range f of ~65 atoms, and t is in a range of 15 atoms 4 or less.
式ＲｒＮｉｓで表わされる好ましい組成はＴ ａ ３５
Ｎ ｒ ５Ｗ６５−ｓからＴａ４５ＮｉＳＷ５５． Ｃ
式中Ｓは約６５〜４５原子爆）までで包囲される組成範
囲、及び組成ＴａｒＮｔｓ （式中「は約５５〜５０原
子鴫、Ｓは約５０〜６５原子４）を含む。金属−金属組
成物の結晶化温度は約６５０°〜８００℃の範囲にあり
硬度は約８００〜１１２５ＤＰＨの範囲ｆある。A preferred composition represented by the formula RrNis is T a 35
N r 5W65-s to Ta45NiSW55. C
and the composition TarNts (where S is about 55 to 50 atoms and S is about 50 to 65 atoms).Metal-metal compositions The crystallization temperature of the material is in the range of about 650 DEG to 800 DEG C., and the hardness is in the range of about 800 to 1125 DPH.
この様な′金属ガラスは、高温（約５００°〜６ｏ。Such 'metallic glasses are used at high temperatures (approximately 500° to 60°C).
℃）における耐熱用途に特に有用である。可能性ある用
途としてはこれらの材料の成る種の高温電解槽における
電極として及び複合建造材料における強化線維としての
使用がある。It is particularly useful for heat-resistant applications at temperatures below 30°F (°C). Possible applications include the use of these materials as electrodes in high temperature electrolyzers and as reinforcing fibers in composite construction materials.
不発明の非晶質合金、即ち金属ガラスは水差熱解析ＣＤ
ＴＡ−）倹渣で明かにされるＶ＆に高い熱安定性を保持
する。最高結晶化に対する温度Ｔｃはガラス試料ｔゆる
やかに加熱して特殊な温度（結晶化温度）で過剰の熱が
発生するか否か或は特殊な温度範囲（ガラス転移温度）
を越えると過剰の熱が吸収されるか否かに注目すること
ＫよりＤＴＡから正確に決定することができる。一般的
にいって、あまりよ（限定されないガラス転移温度は最
低の即ち第１の結晶化最高点Ｔｅｌより約５０°以内下
にあると考えらね、そして慣用の様にそれ以上の温度で
は粘度が約１０１３〜１０１４ボイズの範囲になる温度
範囲を包括する。Uninvented amorphous alloy, i.e. metallic glass, is analyzed by differential thermal analysis CD
TA-) Retains high thermal stability to V& as revealed by sparing. The temperature Tc for maximum crystallization is determined by heating the glass sample slowly and determining whether excessive heat is generated at a special temperature (crystallization temperature) or a special temperature range (glass transition temperature).
It can be more accurately determined from DTA by noting whether excess heat is absorbed beyond K. Generally speaking, the non-limiting glass transition temperature is considered to be within about 50° below the lowest or first crystallization peak Tel, and as is customary, at higher temperatures the viscosity encompasses a temperature range in which the temperature ranges from approximately 10<13> to 10<14> voids.
金属ガラスは溶融物を約１０５〜ｂ
で冷却することによって形成される。平板急冷の箔や急
冷連結Ｉ＋ボタン針金等を造るためには当技術で周知の
様に種々の方法が利用できる。Metallic glasses are formed by cooling the melt at about 10 5 -b. A variety of methods are available, as known in the art, for making plate quench foils, quench connected I+ button wires, and the like.
高い１ｇ性質を示す金属ガラスはまた高い結晶質または
部分的結晶質試料に比べ高い延性と高い耐蝕性を示す。Metallic glasses exhibiting high 1g properties also exhibit high ductility and high corrosion resistance compared to highly crystalline or partially crystalline samples.
その上これらの非晶質合金はかなり高い硬度値をもつ。Moreover, these amorphous alloys have fairly high hardness values.
金属−金属組成物
ま１こ本発明に従えば、−貫したガラス形成挙動に加え
て高い熱安定性を与える金属には’ｌ’ａ Ｎ５ｍＮｂ
−Ｎ ｉ の二成分系、およびＷ、Ｔｉ 及び／
又はＺｒでの三相改質系がある。ここで関心ｉる組成は
一般式ＲｒＮ ＋ ｓＴ ＠またはＲｒＮｉｓで記述さ
れ、ＲはＴａ、Ｎｂ及び／又はＷでＴはＴｉ及び／又は
Ｚｒである。Metal-metal compositions According to the present invention, metals that provide high thermal stability in addition to consistent glass-forming behavior include 'l'a N5mNb.
- binary system of N i and W, Ti and/or
Alternatively, there is a three-phase reforming system with Zr. The composition of interest here is described by the general formula RrN + sT @ or RrNis, where R is Ta, Nb and/or W and T is Ti and/or Zr.
この様な組成物は６５０’−８００℃の範囲の結晶化温
度をもつ。Such compositions have crystallization temperatures in the range of 650'-800°C.
Ｔａ −Ｎｉ 二成分系金属ガラスは７６０°−７８０
℃の範囲で結晶し、Ｎｂ−Ｎｉ系金属ガラスのそれより
約１００℃高い。Ｔａの代りに一部なＷで置換すればＴ
ｃはほんの僅か（約１５〜２０℃）上るだけでＷ含量を
増加しても評価できる様な変化はな−゛＼。Ta-Ni binary metallic glass is 760°-780°
It crystallizes in a temperature range of about 100°C higher than that of Nb-Ni metal glass. If we replace Ta with some W, we get T
There is no appreciable change even if the W content is increased by only a slight increase in c (approximately 15 to 20°C).
一方ＴｉまたはＺｒの部分的添加はＴｃを低下する傾向
がある。On the other hand, partial addition of Ti or Zr tends to lower Tc.
Ｔａ Ｎｉ およびＮｂｒＮｉｓの二成分系について
は Ｓ
ｒが約６５〜６５［子鳴で＄が残りの範囲即ち６５〜６
５原子鴫の時にガラス金属を形成する。For the binary system of TaNi and NbrNis, Sr is about 65-65 [with consonants, $ is in the remaining range i.e. 65-6
Forms glass metal when five atoms are present.
最適の性質はＴａ ｒＮ ｉ ｓの系でｒが約６５〜５
０原子鴫、Ｓが約５０〜６５原子鴫の範囲の時に得られ
る。The optimum properties are in the Ta rN i s system, where r is approximately 65 to 5.
0 atoms are obtained when S is in the range of about 50 to 65 atoms.
Ｔａ３５ＮｉｓＷ６５−ｓ〜Ｔａ４．５ＮｉｓＷ５５−
８の三成分系の範囲については一貫して高いＴｇ と高
い硬度をもつガラス形成範囲はＷＪ１図に示してありこ
れ＆１Ｔａ−Ｗ−Ｎｉの三元組成図である。ａ−ｂ−ｃ
−ｄ−ａで示した多角形は最適ガラス形成区域を包含す
る。この組成区域の外部は実質程度の非晶電性が得られ
ないか或は有利な性質が許容できない程度に減少するか
である。第１（２）でＳは約６５〜４５原子唾の範囲に
ある。Ta35NisW65-s~Ta4.5NisW55-
Regarding the range of the ternary system No. 8, the glass forming range with consistently high Tg and high hardness is shown in Figure WJ1, which is a ternary composition diagram of Ta-W-Ni &1. a-b-c
The polygon labeled -d-a encompasses the optimal glass forming area. Outside this compositional region, either no substantial degree of amorphous electrical properties is available or the beneficial properties are reduced to an unacceptable extent. In No. 1 (2), S is in the range of about 65 to 45 atoms.
ＴｉまたはＺｒはＴｃを低下する傾向があるからこの様
な添加は高いＴｇ及び高い硬度を保持するためには約１
５原子鴫を越ゆべきでなく、そして好ましくは１０憾を
越ゆべきでない。Since Ti or Zr tends to lower Tc, such additions are necessary to maintain high Tg and high hardness.
There should be no more than 5 atoms, and preferably no more than 10 atoms.
一般的にいって前記の系の硬度は約８００〜１１２５Ｄ
ＰＨの範囲にある。Generally speaking, the hardness of the above system is about 800-1125D
In the PH range.
実施例
金属−金属組成物
高温度反応性合金の溶融および液体急冷用の空気電弧−
平板装置を使った。この装置は従来の電弧溶融ボタジ式
炉を不活性雰囲気下での合金の「ハンマーと金敷」型平
板急冷ができるように改造したものであるが、これは４
インチの拡散ポンプ系に連結した不銹鋼量を包含する。Examples Metals - Air arc for melting and liquid quenching of metal compositions high temperature reactive alloys -
A flat plate device was used. This equipment is a conventional electric arc melting furnace modified to enable "hammer and anvil" flat plate quenching of alloys in an inert atmosphere.
Includes a quantity of stainless steel connected to an inch diffusion pump system.
急冷は、その室の床上に平面状の水冷された鋼輿炉床と
溶融合令上に構えた空気駆動の銅塊製ノ１ンマーとを備
えることにより遂行される。慣用の様に電弧溶融は室の
頂部を貫通して挿入されたタングステンの先端を備えた
銅製軸を負Ｊｆ バイアスしかつ呈の底を正にバイアス
することにより完遂される。Ｐを含有する合金は粉成分
を焼結し次いで電弧溶融して均一化することにより造ら
れた。すべての他の合金は成分元素の反復１弧溶融によ
り直接造られた。唯一個の合金ボタン（約２００１１１
９）が再溶融されそれから溶融池の直上に置かれタノ）
ンマーで厚さ約０．００４インチの箔に「衝撃−急冷−
Ｉされた。この方法で得られた冷却速度は約り０〜１０
℃／秒であった。箔はＸ線廻折とＤＴＡで非晶質層が試
験された。Quenching is accomplished by equipping the chamber with a planar water-cooled steel hearth on the floor and an air-driven copper ingot nozzle positioned above the melting stage. Conventionally, arc melting is accomplished by negatively biasing a tungsten-tipped copper shaft inserted through the top of the chamber and positively biasing the bottom of the chamber. The P-containing alloy was made by sintering the powder components and then homogenizing them by electric arc melting. All other alloys were made directly by repeated single-arc melting of the constituent elements. Only one alloy button (approximately 200111
9) is remelted and then placed directly above the molten pool.
Shock - quench - onto a foil approximately 0.004 inch thick using
It was done. The cooling rate obtained with this method is approximately 0-10
°C/second. The foil was tested for amorphous layers by X-ray diffraction and DTA.
ハンマーの直下の衝撃急冷された箔は固化後回塑性変形
を受けているかも知れない。然しハンマーからはみ出し
た溶融物から形成された一部の箔は変形されてなく従っ
て硬度その他関連試験のために適した。硬度は対向面間
Ｋ １５６＠の角度を含む底面正方形の角錐形のダイヤ
モンドよりなるビッカース形王子を使ってダイヤモンド
角錐法によって測定した。種々の金属−金属組成物につ
いての結晶化温度および硬度値を第１表に示す。The shock-quenched foil directly under the hammer may have undergone gyroplastic deformation after solidification. However, some of the foil formed from the melt extruding from the hammer was not deformed and was therefore suitable for hardness and other related tests. The hardness was measured by the diamond pyramid method using a Vickers-shaped Oji made of pyramidal diamond with a square bottom including an angle of K 156@ between opposing surfaces. Crystallization temperatures and hardness values for various metal-metal compositions are shown in Table 1.
′第 １ 表
金属−金属系についての結晶化温度
例 組成 硬さ
原子％ Ｔｃｌ、’ＣＤＰＨＩ Ｔａ５５
Ｎｉｔ５ ７８０ １１１１２ Ｔ
ａ５ＯＮｉ５０ ７６７ ９４１．１１
１５６Ｔａ４５Ｎｉ４５Ｗ１ｏ７９７・８１８．９６９
４ Ｔａ、６Ｎｉ、。Ｗ２Ｂ ７９６
−−−−５ Ｔａ４５Ｎｉ３５Ｗ２ｏ８００
−−−−６ Ｔａ、５Ｎｉ、５Ｗ２ｏ７９１
−＋７ Ｔａ３５Ｎｉ３５Ｗ３０ ｓ
ｏｏ −一−−８Ｔａ５５Ｎｊ３６Ｚｒ１６
６８５ −−９ Ｔ”５５Ｎ’３５”’
１０ ７０９ −１０ Ｔａ５６Ｎｊ
４ｇＴ１１６ ７１７ −一一一１１Ｎｂ６
５Ｎｉ３５６６２９ｇ０
１２ Ｎｂ、、Ｎｉ４ｏ６８０ ９２５１５
Ｎｂ、ｏＮｔｓｏ ６５３ ８６５１
４Ｎｂ６ｏＮｉ２８Ｔｉ１２６６２−−ｍ−'Table 1 Examples of crystallization temperatures for metal-metal systems Composition Hardness atomic % Tcl, 'CDPHI Ta55
Nit5 780 11112 T
a5ONi50 767 941.11
156Ta45Ni45W1o797・818.969
4 Ta, 6 Ni,. W2B 796
-----5 Ta45Ni35W2o800
---6 Ta, 5Ni, 5W2o791
-+7 Ta35Ni35W30s
oo -1--8Ta55Nj36Zr16
685 --9 T"55N'35"'
10 709 -10 Ta56Nj
4gT116 717 -11111Nb6
5Ni356629g0 12 Nb,, Ni4o680 92515
Nb, oNtso 653 8651
4Nb6oNi28Ti12662--m-
第１図は金属−金属系Ｔａ−ＷＮｉの原子鴫で表わした
三元組成２図である。
出願 人 丁ライト１・コーポレーション葬、ｌ凹
ｌ
第１頁の続き
０発 明 者 カール・フランクリン・クライン
アメリカ合衆国ニューシャーシ
ー州０７９４５メンダム・マウンテ
インサイド・ロード（番地無）FIG. 1 is a two-dimensional diagram of the ternary composition represented by atoms of the metal-metal system Ta-WNi. Applicant: Wright 1 Corporation, Inc. Page 1 continued 0 Inventor: Carl Franklin Klein Mendham Mountainside Road, New Chassis, 07945, United States (no street address)
Claims (1)
らなる群より選ばれる少なくとも１つの元素であり、ｒ
は６５〜６５原子唾であり、Ｓは６５〜６５原子優であ
り、ｒとＳとの合計は１００である。）で表わされる組
成を有し、かつ、６５０℃〜８００℃の範囲内の結晶化
温度と８００〜１１２５ＤＰＨの範囲内の硬度を有する
ことを特徴とする、少な（とも５０釜が非晶質であり、
高い結晶化温度および高い硬度を有ｆる非晶質金属合金
。 ；２１式ＲｒＮｔｓＴｌ （ただし、 Ｒ＆エタンタル、ニオブおよびタングステ
ンからなる群より選ばれる少なくとも１つの元素であり
、Ｔはチタンおよびジルコニウムからなる群より選ばれ
る少な（とも１つの元素であり、ｒは６５〜６５原子鴫
であり、Ｓは２５〜６５原子憾であり、ｔは１５原子嶋
以下でありｓｒｓ＠およびｔの合計は１００である。）
で表わされる組ｆＩｔ′ｔｌ−有し、かつ６５０℃〜８
００℃の範囲内の結晶、化温度と８００〜１１２５ＤＰ
Ｈの範囲内の硬度を有することを特徴とする、少な（と
も５０傷が非晶質であり高い結晶化温度および高い硬度
を有する非晶質金属合金。[Claims] (Formula II RrNII (wherein R is at least one element selected from the group consisting of tantalum, niobium and tungsten, and r
has 65 to 65 atoms, S has 65 to 65 atoms, and the sum of r and S is 100. ), and is characterized by having a crystallization temperature within the range of 650°C to 800°C and a hardness within the range of 800 to 1125 DPH. can be,
Amorphous metal alloys with high crystallization temperatures and high hardness. ;21 Formula RrNtsTl (However, R is at least one element selected from the group consisting of etantalum, niobium, and tungsten, T is at least one element selected from the group consisting of titanium and zirconium, and r is 65 to 65 atoms, S is 25 to 65 atoms, t is 15 atoms or less, and the sum of srs@ and t is 100.)
It has the set fIt'tl- represented by, and 650°C ~ 8
Crystallization temperature within the range of 00℃ and 800~1125DP
An amorphous metal alloy having a high crystallization temperature and high hardness, characterized in that it has a hardness in the range of H.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US49545874A | 1974-08-07 | 1974-08-07 | |
| US495458 | 1990-03-16 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS5891144A true JPS5891144A (en) | 1983-05-31 |
| JPS6028899B2 JPS6028899B2 (en) | 1985-07-08 |
Family
ID=23968714
Family Applications (2)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP7714675A Expired JPS5811500B2 (en) | 1974-08-07 | 1975-06-24 | Amorphous metal alloy with high crystallization temperature and high hardness value |
| JP19070082A Expired JPS6028899B2 (en) | 1974-08-07 | 1982-10-29 | Amorphous metal alloy with high crystallization temperature and high hardness |
Family Applications Before (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP7714675A Expired JPS5811500B2 (en) | 1974-08-07 | 1975-06-24 | Amorphous metal alloy with high crystallization temperature and high hardness value |
Country Status (6)
| Country | Link |
|---|---|
| JP (2) | JPS5811500B2 (en) |
| CA (1) | CA1048815A (en) |
| DE (1) | DE2534379C2 (en) |
| FR (1) | FR2281434A1 (en) |
| GB (1) | GB1476589A (en) |
| IT (1) | IT1046075B (en) |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61210143A (en) * | 1985-03-14 | 1986-09-18 | Mitsui Eng & Shipbuild Co Ltd | Amorphous alloy having high corrosion resistance |
| JPS6233735A (en) * | 1985-08-06 | 1987-02-13 | Mitsui Eng & Shipbuild Co Ltd | Amorphous alloy having high corrosion resistance |
| JPS62214148A (en) * | 1986-03-17 | 1987-09-19 | Nec Corp | Amorphous alloy |
| JPS62235448A (en) * | 1986-04-03 | 1987-10-15 | Nec Corp | Amorphous alloy |
| JPS63259043A (en) * | 1987-04-16 | 1988-10-26 | Agency Of Ind Science & Technol | Nickel based alloy for diffusion bonding and its production |
| JPH01132730A (en) * | 1987-11-19 | 1989-05-25 | Agency Of Ind Science & Technol | Insert material of nickel-base super alloy for solid-state welding and solid-state welding method |
| JP2016053207A (en) * | 2014-09-04 | 2016-04-14 | キヤノン株式会社 | Amorphous alloy, molding die and method for producing optical element |
Families Citing this family (15)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3856513A (en) * | 1972-12-26 | 1974-12-24 | Allied Chem | Novel amorphous metals and amorphous metal articles |
| DE2719988C2 (en) * | 1977-05-04 | 1983-01-05 | Siemens AG, 1000 Berlin und 8000 München | Amorphous metal layer containing tantalum, temperature-stable at least up to 300 degrees C, and process for its production |
| CH622380A5 (en) * | 1977-12-21 | 1981-03-31 | Bbc Brown Boveri & Cie | |
| EP0002923B1 (en) * | 1978-01-03 | 1981-11-11 | Allied Corporation | Iron group transition metal-refractory metal-boron glassy alloys |
| JPS6030734B2 (en) * | 1979-04-11 | 1985-07-18 | 健 増本 | Amorphous alloy containing iron group elements and zirconium with low brittleness and excellent thermal stability |
| US4544473A (en) * | 1980-05-12 | 1985-10-01 | Energy Conversion Devices, Inc. | Catalytic electrolytic electrode |
| US4743513A (en) * | 1983-06-10 | 1988-05-10 | Dresser Industries, Inc. | Wear-resistant amorphous materials and articles, and process for preparation thereof |
| DE3616008C2 (en) * | 1985-08-06 | 1994-07-28 | Mitsui Shipbuilding Eng | Highly corrosion-resistant, glass-like alloy |
| JPS63312965A (en) * | 1987-06-16 | 1988-12-21 | Meidensha Electric Mfg Co Ltd | Highly corrosion resistant coated material |
| JPH03267355A (en) * | 1990-03-15 | 1991-11-28 | Sumitomo Electric Ind Ltd | Aluminum-chromium alloy and its production |
| KR100289088B1 (en) * | 1998-12-02 | 2001-05-02 | 박인복 | Method for manufacturing alloy material for electrode tip of plasma generator |
| DE102018113340B4 (en) | 2018-06-05 | 2020-10-01 | Otto-Von-Guericke-Universität Magdeburg | Density-optimized molybdenum alloy |
| DE102018115815A1 (en) * | 2018-06-29 | 2020-01-02 | Universität des Saarlandes | Device and method for producing a cast part formed from an amorphous or partially amorphous metal, and cast part |
| CN114959397B (en) * | 2022-04-28 | 2023-04-07 | 长沙惠科光电有限公司 | Alloy target material, preparation method and application thereof, and array substrate |
| WO2024046742A1 (en) | 2022-08-29 | 2024-03-07 | Universität des Saarlandes | Alloy for producing bulk metallic glasses and shaped bodies therefrom |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3427154A (en) * | 1964-09-11 | 1969-02-11 | Ibm | Amorphous alloys and process therefor |
| US3856513A (en) * | 1972-12-26 | 1974-12-24 | Allied Chem | Novel amorphous metals and amorphous metal articles |
-
1975
- 1975-05-23 GB GB2281475A patent/GB1476589A/en not_active Expired
- 1975-06-24 JP JP7714675A patent/JPS5811500B2/en not_active Expired
- 1975-07-16 FR FR7522266A patent/FR2281434A1/en active Granted
- 1975-07-24 IT IT6892875A patent/IT1046075B/en active
- 1975-08-01 DE DE19752534379 patent/DE2534379C2/en not_active Expired
- 1975-08-06 CA CA75232901A patent/CA1048815A/en not_active Expired
-
1982
- 1982-10-29 JP JP19070082A patent/JPS6028899B2/en not_active Expired
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61210143A (en) * | 1985-03-14 | 1986-09-18 | Mitsui Eng & Shipbuild Co Ltd | Amorphous alloy having high corrosion resistance |
| JPS6233735A (en) * | 1985-08-06 | 1987-02-13 | Mitsui Eng & Shipbuild Co Ltd | Amorphous alloy having high corrosion resistance |
| JPH0535212B2 (en) * | 1985-08-06 | 1993-05-26 | Mitsui Zosen Kk | |
| JPS62214148A (en) * | 1986-03-17 | 1987-09-19 | Nec Corp | Amorphous alloy |
| JPS62235448A (en) * | 1986-04-03 | 1987-10-15 | Nec Corp | Amorphous alloy |
| JPS63259043A (en) * | 1987-04-16 | 1988-10-26 | Agency Of Ind Science & Technol | Nickel based alloy for diffusion bonding and its production |
| JPH0356289B2 (en) * | 1987-04-16 | 1991-08-27 | ||
| JPH01132730A (en) * | 1987-11-19 | 1989-05-25 | Agency Of Ind Science & Technol | Insert material of nickel-base super alloy for solid-state welding and solid-state welding method |
| JP2016053207A (en) * | 2014-09-04 | 2016-04-14 | キヤノン株式会社 | Amorphous alloy, molding die and method for producing optical element |
Also Published As
| Publication number | Publication date |
|---|---|
| CA1048815A (en) | 1979-02-20 |
| IT1046075B (en) | 1980-06-30 |
| DE2534379C2 (en) | 1984-09-13 |
| JPS6028899B2 (en) | 1985-07-08 |
| JPS5120011A (en) | 1976-02-17 |
| FR2281434A1 (en) | 1976-03-05 |
| FR2281434B1 (en) | 1978-10-13 |
| DE2534379A1 (en) | 1976-02-19 |
| GB1476589A (en) | 1977-06-16 |
| JPS5811500B2 (en) | 1983-03-03 |
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