JPH0542499B2 - - Google Patents
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- Publication number
- JPH0542499B2 JPH0542499B2 JP16872983A JP16872983A JPH0542499B2 JP H0542499 B2 JPH0542499 B2 JP H0542499B2 JP 16872983 A JP16872983 A JP 16872983A JP 16872983 A JP16872983 A JP 16872983A JP H0542499 B2 JPH0542499 B2 JP H0542499B2
- Authority
- JP
- Japan
- Prior art keywords
- atomic
- strain
- electrical resistance
- alloy
- strain gauge
- Prior art date
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- 239000000956 alloy Substances 0.000 claims description 37
- 238000000034 method Methods 0.000 claims description 15
- 229910052782 aluminium Inorganic materials 0.000 claims description 13
- 239000007788 liquid Substances 0.000 claims description 13
- 229910052710 silicon Inorganic materials 0.000 claims description 11
- 238000010791 quenching Methods 0.000 claims description 9
- 230000000171 quenching effect Effects 0.000 claims description 9
- 229910052684 Cerium Inorganic materials 0.000 claims description 6
- 229910052750 molybdenum Inorganic materials 0.000 claims description 6
- 229910052715 tantalum Inorganic materials 0.000 claims description 6
- 229910052727 yttrium Inorganic materials 0.000 claims description 6
- 229910052758 niobium Inorganic materials 0.000 claims description 5
- 229910052735 hafnium Inorganic materials 0.000 claims description 4
- 229910052742 iron Inorganic materials 0.000 claims description 2
- 229910000640 Fe alloy Inorganic materials 0.000 claims 1
- 239000000463 material Substances 0.000 description 17
- 230000035945 sensitivity Effects 0.000 description 16
- 229910045601 alloy Inorganic materials 0.000 description 13
- 229910052802 copper Inorganic materials 0.000 description 10
- 239000010949 copper Substances 0.000 description 10
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 8
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 7
- 238000009987 spinning Methods 0.000 description 7
- 230000000052 comparative effect Effects 0.000 description 5
- 238000005096 rolling process Methods 0.000 description 5
- 229910052786 argon Inorganic materials 0.000 description 4
- 238000005260 corrosion Methods 0.000 description 4
- 230000007797 corrosion Effects 0.000 description 4
- 239000007789 gas Substances 0.000 description 4
- 238000004519 manufacturing process Methods 0.000 description 4
- 229910052751 metal Inorganic materials 0.000 description 4
- 239000002184 metal Substances 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 4
- 229910002060 Fe-Cr-Al alloy Inorganic materials 0.000 description 3
- 229910052804 chromium Inorganic materials 0.000 description 3
- 239000000110 cooling liquid Substances 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 229910052748 manganese Inorganic materials 0.000 description 3
- 229910052759 nickel Inorganic materials 0.000 description 3
- 102100036439 Amyloid beta precursor protein binding family B member 1 Human genes 0.000 description 2
- 101000928670 Homo sapiens Amyloid beta precursor protein binding family B member 1 Proteins 0.000 description 2
- 229910018487 Ni—Cr Inorganic materials 0.000 description 2
- 229910052776 Thorium Inorganic materials 0.000 description 2
- 239000000654 additive Substances 0.000 description 2
- 230000000996 additive effect Effects 0.000 description 2
- 229910052791 calcium Inorganic materials 0.000 description 2
- 230000002349 favourable effect Effects 0.000 description 2
- 229910052732 germanium Inorganic materials 0.000 description 2
- 239000012770 industrial material Substances 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 239000010979 ruby Substances 0.000 description 2
- 229910001750 ruby Inorganic materials 0.000 description 2
- 229910052720 vanadium Inorganic materials 0.000 description 2
- 229910052726 zirconium Inorganic materials 0.000 description 2
- 229910001260 Pt alloy Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 229910052787 antimony Inorganic materials 0.000 description 1
- 229910052785 arsenic Inorganic materials 0.000 description 1
- 229910052796 boron Inorganic materials 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 238000010622 cold drawing Methods 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 229910052733 gallium Inorganic materials 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 229910052738 indium Inorganic materials 0.000 description 1
- 239000011261 inert gas Substances 0.000 description 1
- 238000002347 injection Methods 0.000 description 1
- 239000007924 injection Substances 0.000 description 1
- 229910052741 iridium Inorganic materials 0.000 description 1
- WABPQHHGFIMREM-UHFFFAOYSA-N lead(0) Chemical compound [Pb] WABPQHHGFIMREM-UHFFFAOYSA-N 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 229910052697 platinum Inorganic materials 0.000 description 1
- BASFCYQUMIYNBI-UHFFFAOYSA-N platinum Substances [Pt] BASFCYQUMIYNBI-UHFFFAOYSA-N 0.000 description 1
- 238000004080 punching Methods 0.000 description 1
- 238000007712 rapid solidification Methods 0.000 description 1
- 238000005507 spraying Methods 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 229910052718 tin Inorganic materials 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
Landscapes
- Measurement Of Length, Angles, Or The Like Using Electric Or Magnetic Means (AREA)
Description
本発明は、ひずみゲージ特性に優れたFe系合
金材料に関するものである。
一般に知られているように、ひずみゲージは抵
抗素子を伸び縮みさせると、その抵抗値が増減す
るという原理に基づいており、任意の構造物に対
して、静的、動的あるいは衝撃的な応力測定が可
能であり、またゲージの構造が非常に簡単で、か
つ小型化が可能なため、工業的に各種分野に用い
られている。ひずみゲージ用材料として必要な条
件、すなわちひずみゲージ特性として(1)ひずみ感
度（ゲージフアクター）が大きいこと、(2)電気抵
抗値が高いこと、(3)抵抗温度係数が小さく、広い
温度範囲にわたつて一定であること、(4)リード線
材に対する熱起電力が小さいこと、(5)線引き、圧
延加工が容易であること、(6)耐食性があること、
(7)経年変化が極めて小さいこと等があげられる。
現在、ひずみゲージとして用いられている材料
の中でも、ひずみの感度が6.0と大きい白金合金
（Pt90原子％、Ir10原子％）は、電気抵抗の温度
係数が800×10-6K-1と大変大きい。同様にひず
み感度が3.5〜3.6と大きいアイソ・エラステイツ
ク（Fe53原子％、Ni35原子％、Cr9原子％、Mn
＋Mo3原子％）も、電気抵抗温度係数が450×
10-6K-1とかなり大きい。また、抵抗温度係数が
±10×10-6K-1と小さいカルマ（Ni61原子％、
Cr21原子％、Al＋Fe9原子％）はひずみ感度が
2.4と小さく、同様にアドバンス（Cu52原子％、
Ni46原子％、Mn1原子％、Fe0.6原子％）も、電
気抵抗温度係数は20×10-6K-1と小さいが、ひず
み感度は2.0でしかない。しかも、アドバンスは
さらに対銅熱起電力が43μV／Ｋと極めて高いと
いう欠点も有している。
また、特殊用ひずみゲージとして、高温用及び
極低温用ひずみゲージがある。高温に耐える抵抗
体は電気抵抗温度係数が大きいのが通例で、常温
からの温度変化と、大きな電気抵抗温度係数によ
り、極めて大きな見掛けひずみを生じ、その補正
はかなり困難である。また、現在極抵温用ひずみ
ゲージに使用されているNi−Cr合金及び安定化
Fe−Cr−Al合金系の材料は温度変化によるひず
みゲージ特性への影響が大きいという欠点を有し
ており、ひずみゲージ材料としては不十分であ
る。
このように、ひずみゲージ用材料としての必要
条件を大体満足している材料が一応実用に供され
ているが、当業界ではさらにひずみ感度が大き
く、電気抵抗の温度係数が小さく、リード線に対
する熱起電力が小さい等、ひずみゲージ特性をよ
り向上させたひずみゲージ用材料の出現が待ち望
まれている。
そこで、本発明者らはこれらの事情に鑑み、ひ
ずみゲージ特性に優れたFe系合金材料を提供す
ることを目的として鋭意研究した結果、特定の組
成からなるFe系合金を溶湯状態から急冷固化す
ると、現用材に比べ、はるかにひずみゲージ特性
に優れた合金材料が得られることを見い出し、本
発明を完成した。
すなわち、本発明は、液体急冷法によつて得ら
れ、Crが10〜41原子％で、Al又はSiからなる群
より選ばれた１種又は２種の元素が7.5〜17.5原
子％で、残部が実質的にFeからなるひずみゲー
ジ特性に優れたFe系合金材料及び液体急冷法に
よつて得られ、Crが10〜41原子％で、Al又はSi
からなる群より選ばれた１種又は２種の元素が
7.5〜17.5原子％で、40原子％以下のNi、10原子
％以下のCo、Nb、Ta、Mo及びCu、1.0原子％
以下のHf、Ce及びＹからなる群より選ばれた１
種の元素を含有し、残部が実質的にFeからなる
ひずみゲージ特性に優れたFe系合金材料である。
本発明の合金材料について説明すると、Crが
10〜41原子％で、Al又はSiが7.5〜17.5原子％必
要で、好ましくは12.5〜32.5原子％、10〜17.5原
子％である。Crが10原子％未満、Al又はSiが7.5
原子％未満では、電気抵抗は低下し、また電気抵
抗温度係数も大きくなり、しかも耐食性、耐疲労
性、機械的性能、耐酸化性も向上させることはで
きず、ひずみゲージとしての必要な条件を満たす
ことができなくなる。また、Crが41原子％より
多い場合及びAl又はSiが17.5原子％より多い場合
は、電気抵抗温度係数も極端に増大し、ひずみゲ
ージとしての特性は低下する。
本発明の合金材料にNi、Co、Nb、Ta、Ｖ、
Mo、Mn、Cu、Ge、Ga、Ti、Zr、Hf、Ca、
Ce、Ｙ及びThからなる群より選ばれた１種又は
２種以上の元素を40原子％以下添加すると（ただ
し、Niは40原子％以下、Co、Nb、Ta、Ｖ、
Mo、Mn、Cu、Ge及びGaはそれぞれ10原子％以
下、Ti、Zr、Hf、Ca、Ce、Ｙ及びThはそれぞ
れ1.0原子％以下である。）、電気抵抗及び電気抵
抗温度係数、耐食性等ひずみゲージに必要な特性
を向上させることができる。しかし、上記した添
加元素量を超えて添加すると、冷間加工性が低下
し、脆くなり、実用に供しなくなる。
また、上記総ての合金系において、通常の工業
材料中に存在する程度の不純物、例えばＢ、Ｐ、
Ｃ、Ｓ、Sn、In、As、Sb等が少量含まれていて
も、本発明を達成するにはなんら支障をきたすも
のではない。
本発明の合金を製造するには、前記合金組成を
用い、不活性ガス雰囲気中あるいは真空中で加熱
溶融した後、液体急冷法で急冷凝固させることが
必要である。その液体急冷法としては、片ロール
法、双ロール法及び回転液中紡糸法が特に有用で
ある。片ロール法、双ロール法は冷却温度105〜
106℃／secを有しており、薄帯状材料を製造する
ことができる。また、回転液中紡糸法としては、
特開昭56−165016号公報に記載されているよう
に、回転するドラム中に水膜を形成させ、この水
膜の中に溶融状態の金属を紡糸ノズルを通して噴
出し、円形断面を有する連続細線を得る方法があ
げられる。この回転液中紡糸法において、特に均
一な連続細線を製造する場合には、回転するドラ
ムの周速度を噴出された溶融金属流の速度よりも
５〜30％程度速くすることが望まれ、また水膜と
噴出された溶融金属流とのなす角度は20゜以上が
好ましい。
本発明の合金材料は、冷間加工を連続して行う
ことができ、寸法精度及び機械的性質をより向上
させることができる。また、必要に応じて焼なま
し等の熱処理をも行うことができ、より一層ひず
みゲージ特性を安定化させることができる。この
ような液体急冷法の高速化、工程の単純さは、本
発明の合金材料を製造するに際して、製造コスト
の低減、省エネルギーといつた効果をももたら
す。
このように液体急冷法により得られた本発明の
合金材料は、先に記したような従来のNi−Cr系
合金及びFe−Cr−Al系合金等と比較してさらに
向上したひずみゲージ特性を有する。一例をあげ
るならば、Fe65原子％、Cr20原子％、Al15原子
％からなる、急冷凝固により得られた本発明の
Fe−Cr−Al合金材料は、150.0μΩ・cmと高い電
気抵抗値を有し、ひずみ感度は3.7と非常に高く
なつている〔従来のアーマアロイＤ（Fe62原子
％、Cr20原子％、Al18原子％）は1.3〜3.0と低
い。〕。また、本発明のFe65原子％、Cr20原子％、
Al15原子％組成合金の対銅熱起電力は−
1.21μV／Ｋとかなり小さく、さらにひずみ率の
変化がひずみ感度に与える影響も小さい。ひずみ
ゲージとして重要な特性のひとつである電気抵抗
温度係数も２×10-6K-1と非常に小さく、それと
比較してアーマアロイＤは250×10-6K-1とかな
り大きい。また、冷間線引きやアーマアロイＤで
は、困難な冷間圧延加工も容易であり、良好な耐
食性も有している。特に、液体急冷法により得ら
れる薄帯状の合金材料は、厚さが10〜20μmで、
圧延により表裏両面を平担にしたあと打ち抜き加
工が簡単にでき、また細線状材料は容易に冷間線
引きが可能で、線径25μm程度以下に加工するこ
とができ、ひずみゲージ用材料を製造する上にお
いても非常に好ましい。
また、本発明合金材料は、極低温及び高温にお
けるひずみゲージ特性にも非常に優れている。例
えば上記Fe65原子％、Cr20原子％、Al15原子％
組成の合金において、電気抵抗値は−196℃では、
150.5μΩ・cm、０℃では150.0μΩ・cm、300℃で
は150.2μΩ・cm、900℃では150.3μΩ・cmと極低
温から高温に至るまで、電気抵抗値はほとんど変
化せず、また電気抵抗の温度係数も−196℃〜０
℃では、17×10-6K-1、０℃〜900℃では、２×
10-6K-1と広温度域にわたつて極めて小さな値で
あり、温度変化からくるひずみによる誤差も極端
に小さい。また、温度変化によるひずみ感度への
影響は１％以下と極めて小さく、極低温域及び高
温域においても使用に供することが可能な合金材
料である。
このように、本発明の合金材料はひずみゲージ
特性に優れた材料として、工業用材料に有用なも
のであり、広く使用することができる。
次に、本発明を実施例により具体的に説明す
る。
実施例１〜25、比較例１〜26
表１に示す各種組成よりなるFe−Cr−（Al、
Si）元素及びFe−Cr−（Al、Si）−Ｍ（Ｍは、Ni、
Co、Nb、Ta、Mo、Cu、Hf、Ce及びＹからな
る群より選ばれた１種を表す）元素を、アルゴン
ガス雰囲気中で溶融した後、アルゴンガス噴出圧
1.5Kg／cm2で、孔径0.30mmφのルビー製ノズルよ
り、4000rpmで回転している直径20cmの鋼鉄ロー
ル表面に噴出して厚さ10〜20μm（幅３mm）の連続
した薄帯状材料を製造した。
これら薄帯状の合金材料について、ひずみゲー
ジ特性として、四端子法での電気抵抗（μΩ・
cm）、０℃から900℃までの温度範囲における電気
抵抗温度係数（K-1）、ひずみ感度（ひずみ感度
ＫはＫ＝dR／Ｒ・１／εで求めたものであり、
ここでＲはひずみをかけない時の抵抗体の電気抵
抗、dRはひずみをかけた時の電気抵抗の変化分、
εはひずみを表す。）、対銅熱起電力（μV／Ｋ）
及び180゜密着曲げ性について測定した。
その結果を表１に示す。
なお、比較のため、現在使用されている合金材
料（比較例１〜４）についても表１に示す。
The present invention relates to an Fe-based alloy material with excellent strain gauge properties. As is generally known, strain gauges are based on the principle that when a resistance element is expanded or contracted, its resistance value increases or decreases. It is used industrially in various fields because it allows measurement, has a very simple gauge structure, and can be miniaturized. The conditions required for a material for strain gauges, namely strain gauge characteristics, are (1) high strain sensitivity (gauge factor), (2) high electrical resistance, and (3) low temperature coefficient of resistance and wide temperature range. (4) The thermoelectromotive force on the lead wire material is small. (5) It is easy to draw and roll the wire. (6) It has corrosion resistance.
(7) Changes over time are extremely small. Among the materials currently used as strain gauges, platinum alloy (90 atomic % Pt, 10 atomic % Ir) has a high strain sensitivity of 6.0, and a very large temperature coefficient of electrical resistance of 800 × 10 -6 K -1 . . Similarly, isoelastic materials with high strain sensitivity of 3.5 to 3.6 (Fe53 at%, Ni35 at%, Cr9 at%, Mn
+Mo3 atomic%) also has an electrical resistance temperature coefficient of 450×
It is quite large at 10 -6 K -1 . In addition, Karma ( Ni61 atomic %,
Cr21 atomic%, Al+Fe9 atomic%) have strain sensitivity.
Small as 2.4, similarly advanced (Cu52 atomic%,
Ni46 atomic%, Mn1 atomic%, Fe0.6 atomic%) also have a small electrical resistance temperature coefficient of 20×10 -6 K -1 , but their strain sensitivity is only 2.0. Moreover, Advance also has the disadvantage that its thermal electromotive force against copper is extremely high at 43 μV/K. Further, as special strain gauges, there are strain gauges for high temperature and cryogenic temperature. Resistors that can withstand high temperatures usually have a large temperature coefficient of electrical resistance, and a temperature change from room temperature and a large temperature coefficient of electrical resistance cause an extremely large apparent strain, which is quite difficult to correct. In addition, we will introduce the Ni-Cr alloy currently used in cryogenic strain gauges and the stabilizing
Fe-Cr-Al alloy materials have the disadvantage that strain gauge characteristics are greatly affected by temperature changes, and are therefore unsatisfactory as strain gauge materials. In this way, materials that generally satisfy the requirements for strain gauge materials are in practical use, but in this industry, they have even higher strain sensitivity, a lower temperature coefficient of electrical resistance, and a higher temperature coefficient for lead wires. The emergence of strain gauge materials with improved strain gauge characteristics such as low electromotive force is eagerly awaited. In view of these circumstances, the inventors of the present invention conducted intensive research with the aim of providing an Fe-based alloy material with excellent strain gauge properties, and as a result, they found that when an Fe-based alloy with a specific composition is rapidly solidified from a molten state, discovered that an alloy material with far superior strain gauge properties could be obtained compared to currently used materials, and completed the present invention. That is, the present invention is obtained by a liquid quenching method, Cr is 10 to 41 atomic %, one or two elements selected from the group consisting of Al or Si is 7.5 to 17.5 atomic %, and the remainder is is obtained by using an Fe-based alloy material with excellent strain gauge properties consisting essentially of Fe and a liquid quenching method, with a Cr content of 10 to 41 at% and Al or Si.
One or two elements selected from the group consisting of
7.5 to 17.5 at%, up to 40 at% Ni, up to 10 at% Co, Nb, Ta, Mo and Cu, 1.0 at%
1 selected from the group consisting of Hf, Ce and Y below
It is an Fe-based alloy material that has excellent strain gauge properties and contains certain elements and the remainder is essentially Fe. To explain the alloy material of the present invention, Cr is
10 to 41 atomic %, and 7.5 to 17.5 atomic % of Al or Si is required, preferably 12.5 to 32.5 atomic %, and 10 to 17.5 atomic %. Cr less than 10 at%, Al or Si 7.5
If it is less than atomic percent, the electrical resistance will decrease and the electrical resistance temperature coefficient will increase, and corrosion resistance, fatigue resistance, mechanical performance, and oxidation resistance cannot be improved, and the necessary conditions for strain gauges cannot be improved. become unable to satisfy. Further, when Cr is more than 41 atomic % and when Al or Si is more than 17.5 atomic %, the temperature coefficient of electrical resistance increases extremely, and the characteristics as a strain gauge deteriorate. The alloy material of the present invention includes Ni, Co, Nb, Ta, V,
Mo, Mn, Cu, Ge, Ga, Ti, Zr, Hf, Ca,
When one or more elements selected from the group consisting of Ce, Y, and Th are added at 40 atomic % or less (with the exception of 40 atomic % or less for Ni, Co, Nb, Ta, V,
Mo, Mn, Cu, Ge, and Ga are each 10 atomic % or less, and Ti, Zr, Hf, Ca, Ce, Y, and Th are each 1.0 atomic % or less. ), electrical resistance, temperature coefficient of electrical resistance, corrosion resistance, and other properties necessary for strain gauges can be improved. However, if the amount of additional elements exceeds the above-mentioned amount, the cold workability decreases and the material becomes brittle, making it unusable for practical use. In addition, in all the alloy systems mentioned above, impurities present in ordinary industrial materials, such as B, P,
Even if a small amount of C, S, Sn, In, As, Sb, etc. is contained, this does not pose any problem in achieving the present invention. In order to manufacture the alloy of the present invention, it is necessary to use the above alloy composition, heat and melt it in an inert gas atmosphere or in vacuum, and then rapidly solidify it by a liquid quenching method. Particularly useful as the liquid quenching method are a single roll method, a twin roll method, and a rotating liquid spinning method. For the single roll method and twin roll method, the cooling temperature is 10 5 ~
It has a temperature of 10 6 °C/sec and can produce ribbon-shaped materials. In addition, as a rotating liquid spinning method,
As described in JP-A No. 56-165016, a water film is formed in a rotating drum, and molten metal is ejected into this water film through a spinning nozzle to produce a continuous thin wire having a circular cross section. Here are some ways to get it. In this rotating liquid spinning method, especially when producing a uniform continuous thin wire, it is desirable that the circumferential speed of the rotating drum be approximately 5 to 30% faster than the speed of the ejected molten metal flow. The angle between the water film and the ejected molten metal stream is preferably 20° or more. The alloy material of the present invention can be subjected to continuous cold working, and its dimensional accuracy and mechanical properties can be further improved. In addition, heat treatment such as annealing can be performed as necessary, and the strain gauge characteristics can be further stabilized. The high-speed liquid quenching method and the simplicity of the process also bring about effects such as reduced manufacturing costs and energy savings when manufacturing the alloy material of the present invention. The alloy material of the present invention obtained by the liquid quenching method has improved strain gauge properties compared to the conventional Ni-Cr alloy and Fe-Cr-Al alloy as described above. have To give an example, the present invention obtained by rapid solidification consists of 65 at.% Fe, 20 at.% Cr, and 15 at.% Al.
The Fe-Cr-Al alloy material has a high electrical resistance value of 150.0μΩ・cm and a very high strain sensitivity of 3.7 [Conventional Armor Alloy D (Fe62 atomic%, Cr20 atomic%, Al18 atomic% ) is low at 1.3-3.0. ]. In addition, Fe65 atomic%, Cr20 atomic% of the present invention,
The thermoelectromotive force against copper of Al15 atomic% composition alloy is −
It is quite small at 1.21 μV/K, and the effect of changes in strain rate on strain sensitivity is also small. The temperature coefficient of electrical resistance, which is one of the important characteristics for a strain gauge, is also very small at 2 x 10 -6 K -1 , whereas Armoralloy D's temperature coefficient is quite large at 250 x 10 -6 K -1 . In addition, cold drawing and Armor Alloy D can be easily subjected to difficult cold rolling processes and have good corrosion resistance. In particular, the ribbon-shaped alloy material obtained by the liquid quenching method has a thickness of 10 to 20 μm,
After flattening both the front and back sides by rolling, punching can be easily performed, and thin wire-shaped materials can be easily cold-drawn to a wire diameter of approximately 25 μm or less, making it possible to manufacture materials for strain gauges. The above is also highly preferred. Furthermore, the alloy material of the present invention has excellent strain gauge properties at extremely low temperatures and high temperatures. For example, the above Fe65 at%, Cr20 at%, Al15 at%
In the alloy with the composition, the electrical resistance value at -196℃ is
150.5μΩ・cm, 150.0μΩ・cm at 0℃, 150.2μΩ・cm at 300℃, and 150.3μΩ・cm at 900℃.The electrical resistance value hardly changes from extremely low temperature to high temperature. Temperature coefficient is also -196℃~0
17×10 -6 K -1 at ℃, 2× from 0℃ to 900℃
10 -6 K -1 , which is an extremely small value over a wide temperature range, and the error due to distortion caused by temperature changes is also extremely small. Furthermore, the effect on strain sensitivity due to temperature changes is extremely small, 1% or less, and it is an alloy material that can be used even in extremely low temperature and high temperature ranges. As described above, the alloy material of the present invention is useful as an industrial material as a material with excellent strain gauge characteristics, and can be widely used. Next, the present invention will be specifically explained using examples. Examples 1 to 25, Comparative Examples 1 to 26 Fe-Cr-(Al,
Si) element and Fe-Cr-(Al, Si)-M (M is Ni,
After melting an element selected from the group consisting of Co, Nb, Ta, Mo, Cu, Hf, Ce, and Y in an argon gas atmosphere, the argon gas ejection pressure
A continuous thin strip material with a thickness of 10 to 20 μm (width 3 mm) was produced by spraying 1.5 Kg/cm 2 from a ruby nozzle with a hole diameter of 0.30 mm onto the surface of a 20 cm diameter steel roll rotating at 4000 rpm. . For these thin strip-shaped alloy materials, the electrical resistance (μΩ・
cm), electrical resistance temperature coefficient (K -1 ) in the temperature range from 0°C to 900°C, strain sensitivity (strain sensitivity K is determined by K = dR/R・1/ε,
Here, R is the electrical resistance of the resistor when no strain is applied, and dR is the change in electrical resistance when strain is applied.
ε represents strain. ), thermoelectromotive force against copper (μV/K)
and 180° close bendability were measured. The results are shown in Table 1. For comparison, alloy materials currently used (Comparative Examples 1 to 4) are also shown in Table 1.
【表】【table】
【表】【table】
【表】
表１より明らかなごとく、本発明の実施例１〜
25の合金材料は、適正なCr量、Al量、Si量及び
添加元素量を有しているため、非常に小さい電気
抵抗温度係数、大きなひずみ感度、かなり小さい
対銅熱起電力を有し、ひずみゲージ材料として非
常に好ましい特性を有している。また、比較例１
〜４は、現在ひずみゲージとして用いられている
合金材料であるが、電気抵抗温度係数が小さけれ
ば、ひずみ感度が小さく、対銅熱起電力が大きい
とか、それぞれのひずみゲージとして必要な条件
がすべて満足されてはいない。比較例５〜８は、
Cr及びAl、Siの含有量が適正量外であるため、
電気抵抗も低く、特に電気抵抗温度係数は非常に
大きく、ひずみ感度は小さく、ひずみゲージ用合
金材料としては不満足なものであつた。
さらに、比較例９〜26は、添加する元素の量が
適正量を超えているため、靭性を失い脆くなり実
用に供することは不可能であつた。
実施例 26〜49
表２に示す各種組成よりなるFe−Cr−（Al、
Si）合金及びFe−Cr−（Al、Si）−Ｍ（ＭはNi、
Co、Ta、Mo、Cu、Hf、Ce及びＹからなる群よ
り選ばれた１種を表す。）合金を、アルゴンガス
雰囲気中で溶解した後、アルゴンガス噴出圧4.5
Kg／cm2で、孔径0.115mmφのルビー製紡糸ノズル
より、350rpmで回転している内径50cmφの円筒
ドラム内に形成された温度４℃、深さ25mmの回転
冷却液体水中に噴出して急冷凝固させ、平均直径
0.1mmφの円形断面を有した均一な連続細線を得
た。
この時の紡糸ノズルと回転冷却液体面との距離
は２mmに保持し、ノズルより噴出された溶融金属
流と回転冷却液体面とのなす角は70度であつた。
作製した急冷合金細線のひずみゲージ特性につ
いて、実施例１と同様に、電気抵抗、電気抵抗温
度係数、ひずみ感度、対銅熱起電力及び180度密
着曲げ性について測定したその結果を表２に示
す。[Table] As is clear from Table 1, Examples 1 to 1 of the present invention
The alloy material No. 25 has appropriate Cr content, Al content, Si content, and additive element content, so it has a very small electrical resistance temperature coefficient, large strain sensitivity, and a fairly small thermoelectromotive force against copper. It has very favorable properties as a strain gauge material. Also, comparative example 1
Items 4 to 4 are alloy materials currently used as strain gauges, but if the temperature coefficient of electrical resistance is small, the strain sensitivity is low, and the thermoelectromotive force against copper is large, all of the conditions necessary for strain gauges are met. Not satisfied. Comparative Examples 5 to 8 are
Because the content of Cr, Al, and Si is outside the appropriate amount,
The electrical resistance was low, especially the temperature coefficient of electrical resistance was very large, and the strain sensitivity was low, making it unsatisfactory as an alloy material for strain gauges. Furthermore, in Comparative Examples 9 to 26, since the amount of added elements exceeded the appropriate amount, they lost toughness and became brittle, making it impossible to put them into practical use. Examples 26 to 49 Fe-Cr-(Al,
Si) alloy and Fe-Cr-(Al, Si)-M (M is Ni,
Represents one selected from the group consisting of Co, Ta, Mo, Cu, Hf, Ce, and Y. ) After melting the alloy in an argon gas atmosphere, the argon gas injection pressure was 4.5.
Kg/ cm2 , from a ruby spinning nozzle with a hole diameter of 0.115mmφ, is spouted into a rotating cooling liquid water with a temperature of 4℃ and a depth of 25mm formed in a cylindrical drum with an inner diameter of 50cmφ rotating at 350rpm and rapidly solidified. Let, average diameter
A uniform continuous thin wire with a circular cross section of 0.1 mmφ was obtained. At this time, the distance between the spinning nozzle and the rotating cooling liquid surface was maintained at 2 mm, and the angle between the molten metal flow jetted from the nozzle and the rotating cooling liquid surface was 70 degrees. Regarding the strain gauge properties of the produced rapidly solidified thin alloy wire, the electrical resistance, temperature coefficient of electrical resistance, strain sensitivity, thermoelectromotive force against copper, and 180 degree close bendability were measured in the same manner as in Example 1. The results are shown in Table 2. .
【表】
表２より明らかなごとく、回転液中紡糸法によ
り作製した本発明の実施例26〜49の合金材料は、
適正なCr量、Al量、Si量及び添加元素量を有し
ているため、非常に小さい電気抵抗温度係数、大
きなひずみ感度、かなり小さい対銅熱起電力を有
し、ひずみゲージ材料として非常に好ましい特性
を有している。[Table] As is clear from Table 2, the alloy materials of Examples 26 to 49 of the present invention produced by the rotating liquid spinning method were:
Because it has appropriate amounts of Cr, Al, Si, and additive elements, it has a very small temperature coefficient of electrical resistance, large strain sensitivity, and a fairly small thermoelectromotive force against copper, making it very suitable as a strain gauge material. It has favorable properties.
Claims (1)
子％で、Al又はSiからなる群より選ばれた１種
又は２種の元素が7.5〜17.5原子％で、残部が実
質的にFeからなるひずみゲージ特性に優れたFe
系合金材料。 ２ 液体急冷法によつて得られ、Crが10〜41原
子％で、Al又はSiからなる群より選ばれた１種
又は２種の元素が7.5〜17.5原子％で、40原子％
以下のNi、10原子％以下のCo、Nb、Ta、Mo、
及びCu、1.0原子％以下のHf、Ce及びＹからなる
群より選ばれた１種の元素を含有し、残部が実質
的にFeからなるひずみゲージ特性に優れたFe系
合金材料。[Claims] 1. Obtained by a liquid quenching method, Cr is 10 to 41 atomic %, one or two elements selected from the group consisting of Al or Si are 7.5 to 17.5 atomic %, Fe with excellent strain gauge properties, with the remainder essentially consisting of Fe
alloy material. 2 Obtained by liquid quenching method, Cr is 10 to 41 at%, one or two elements selected from the group consisting of Al or Si are 7.5 to 17.5 at%, and 40 at%
Less than Ni, less than 10 atomic% Co, Nb, Ta, Mo,
An Fe-based alloy material having excellent strain gauge properties, containing one element selected from the group consisting of Hf, Ce, and Y in an amount of 1.0 atomic % or less, and the remainder being substantially Fe.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP16872983A JPS6059048A (en) | 1983-09-13 | 1983-09-13 | Fe alloy material having superior strain gauge characteristic |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP16872983A JPS6059048A (en) | 1983-09-13 | 1983-09-13 | Fe alloy material having superior strain gauge characteristic |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS6059048A JPS6059048A (en) | 1985-04-05 |
| JPH0542499B2 true JPH0542499B2 (en) | 1993-06-28 |
Family
ID=15873333
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP16872983A Granted JPS6059048A (en) | 1983-09-13 | 1983-09-13 | Fe alloy material having superior strain gauge characteristic |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS6059048A (en) |
Families Citing this family (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP5408533B2 (en) * | 2009-05-28 | 2014-02-05 | 独立行政法人国立高等専門学校機構 | Fe-Ni-Cr-based isoelastic composition for strain gauge, and strain gauge manufactured using the composition |
| WO2011089998A1 (en) * | 2010-01-20 | 2011-07-28 | 国立大学法人東北大学 | Ferritic stainless steel for high temperature use |
| JP6025318B2 (en) * | 2011-10-31 | 2016-11-16 | ミネベア株式会社 | Load cell |
| JP6774861B2 (en) * | 2016-12-02 | 2020-10-28 | 公益財団法人電磁材料研究所 | Strain resistance film and strain sensor for high temperature, and their manufacturing method |
-
1983
- 1983-09-13 JP JP16872983A patent/JPS6059048A/en active Granted
Also Published As
| Publication number | Publication date |
|---|---|
| JPS6059048A (en) | 1985-04-05 |
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