JPH0359974B2 - - Google Patents
Info
- Publication number
- JPH0359974B2 JPH0359974B2 JP5357083A JP5357083A JPH0359974B2 JP H0359974 B2 JPH0359974 B2 JP H0359974B2 JP 5357083 A JP5357083 A JP 5357083A JP 5357083 A JP5357083 A JP 5357083A JP H0359974 B2 JPH0359974 B2 JP H0359974B2
- Authority
- JP
- Japan
- Prior art keywords
- constant
- alloy
- modulus
- properties
- constant modulus
- 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.)
- Expired
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- 229910045601 alloy Inorganic materials 0.000 claims description 29
- 239000000956 alloy Substances 0.000 claims description 29
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 14
- 239000010936 titanium Substances 0.000 claims description 11
- 239000011651 chromium Substances 0.000 claims description 9
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 6
- 239000010955 niobium Substances 0.000 claims description 6
- 229910052719 titanium Inorganic materials 0.000 claims description 6
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 5
- 229910052782 aluminium Inorganic materials 0.000 claims description 5
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 5
- 229910052804 chromium Inorganic materials 0.000 claims description 5
- 229910052759 nickel Inorganic materials 0.000 claims description 5
- VSZWPYCFIRKVQL-UHFFFAOYSA-N selanylidenegallium;selenium Chemical compound [Se].[Se]=[Ga].[Se]=[Ga] VSZWPYCFIRKVQL-UHFFFAOYSA-N 0.000 claims description 4
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 3
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims description 3
- 239000012535 impurity Substances 0.000 claims description 3
- 229910052750 molybdenum Inorganic materials 0.000 claims description 3
- 239000011733 molybdenum Substances 0.000 claims description 3
- 229910052758 niobium Inorganic materials 0.000 claims description 3
- 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
- GUVRBAGPIYLISA-UHFFFAOYSA-N tantalum atom Chemical compound [Ta] GUVRBAGPIYLISA-UHFFFAOYSA-N 0.000 claims description 3
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 claims description 3
- 229910052721 tungsten Inorganic materials 0.000 claims description 3
- 239000010937 tungsten Substances 0.000 claims description 3
- 229910052751 metal Inorganic materials 0.000 claims description 2
- 239000002184 metal Substances 0.000 claims description 2
- 150000002739 metals Chemical class 0.000 claims description 2
- 238000009413 insulation Methods 0.000 claims 1
- 239000000463 material Substances 0.000 description 7
- 230000032683 aging Effects 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
- 238000005482 strain hardening Methods 0.000 description 4
- 238000010586 diagram Methods 0.000 description 3
- 238000010438 heat treatment Methods 0.000 description 3
- 238000000034 method Methods 0.000 description 3
- 230000000694 effects Effects 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 229910000942 Elinvar Inorganic materials 0.000 description 1
- 229910001030 Iron–nickel alloy Inorganic materials 0.000 description 1
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 239000011261 inert gas Substances 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- -1 titanium Chemical compound 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Landscapes
- Springs (AREA)
- Moulds For Moulding Plastics Or The Like (AREA)
Description
〔発明の技術分野〕
本発明は精密機器を中心に応用される弾性率の
温度依存性が極めて少ない恒弾性合金に関する。
〔発明の技術的背景とその問題点〕
一般に、恒弾性合金はトルク指示計、時計計測
用ぜんまい等の精密部品、精密ベロー、絶対圧力
計、流量計、工業用圧力計、ブルドン管等の精密
構造部品、或いは音叉音片、発振機等の振動体材
料などの温度変化による弾性率の変化をきらう機
器の材料として広く利用されている。
従来、上述した恒弾性合金としてはFe−Ni系
のエリンバー合金が著名であるが、この材料は冷
間加工状態で使わなければならず、しかも冷間加
工条件が恒弾性特性や機械的特性に大きく影響さ
れるという欠点があつた。
このようなことから、近年はFe−Ni−Cr−Ti
−Al系の析出形の恒弾性合金が多く利用される
ようになつてきた。この析出形の恒弾性合金は、
冷間加工と熱処理条件を選定することにより恒弾
性特性を評価する一つの指標である熱弾性係数
（TEC）を比較的容易に零にすることが可能であ
ると共に、強度的にも優れた特性を示すものであ
る。しかしながら、この析出形恒弾性合金の恒弾
性特性は、通常70〜80℃程度までしか保持でき
ず、高温雰囲気で使用する場合に大きな限界があ
り、その応用範囲も限られていた。
〔発明の目的〕
本発明は上記事情に鑑みなされたもので、恒弾
性特性を130℃以上まで大幅に向上させると共に、
強度的にも従来の析出形恒弾性合金と同等以上の
優れた特性を有する恒弾性合金を提供しようとす
るものである。
〔発明の概要〕
本発明は重量％でニツケル（Ni）40.0〜44.5
％、クロム（Cr）4.0〜6.5％、チタン（Ti）0.5
〜1.9％、アルミニウム（Al）0.1〜1.0％、ジルコ
ニウム（Zr）0.2〜2.0％、残部鉄（Fe）と附随的
不純物よりなることを第１発明とし、更にモリブ
デン（Mo）、ニオブ（Nb）、タンタル（Ta）及
びタングステン（Ｗ）のうちの１種又は２種以上
の金属を0.1〜5.5％添加することを第２発明とす
るものであり、20℃から少なくとも130℃の温度
範囲で熱弾性係数が±20×10-6［１／℃］の恒弾
性特性を有するものである。
次に、本発明の恒弾性合金を構成する各成分の
作用及びその添加量の限定理由について説明す
る。
ニツケル（Ni）は恒弾性特性を維持するため
に最も効果的な元素であり、その添加量が40.0％
未満及び44.5％を越えると、有効な恒弾性特性が
得られない。
クロム（Cr）はニツケルと同様に恒弾性特性
を維持するために有効な元素であり、その添加量
が4.0％未満及び6.5％を越えると、充分な恒弾性
特性が得られない。またクロムの添加は合金の耐
食性の向上の点からも有効である。
チタン（Ti）は時効処理により析出して合金
強度を向上させるのに有効な元素であり、その添
加量が0.5％未満では充分な強度向上が得られず、
かといつて1.99％を越えると、恒弾性特性の劣化
を招く。
アルミニウム（Al）はチタンと同様に合金強
度を向上させるのに有効な元素であり、その添加
量が0.0未満では充分な強度向上を達成できず、
かといつて1.0％を越えると、恒弾性特性の劣化
を招く。
ジルコニウム（Zr）はチタン及びアルミニウ
ムとの複合添加により強度向上に寄与する。こう
したジルコニウムの添加量が0.2％未満では充分
な強度向上を達成できず、かといつて2.0％を越
えると、恒弾性特性の劣化を招く。
更に、モリブデン（Mo）、ニオブ（Nb）、タン
タル（Ta）、タングステン（Ｗ）はその添加量を
0.1〜5.5％の範囲に規定することにより、単独又
は２種以上用いても、恒弾性特性を劣化させるこ
となく、合金の機械的特性の向上を図ることがで
きる。
次に、本発明の恒弾性合金の製造法について簡
単に説明する。
まず、真空又は不活性ガス雰囲気中で誘導溶解
法等により所定の合金組成に溶成し、熱間加工に
より所定形状まで加工する。更に、冷間加工を行
なつて所定の形状にした後、時効処理を施して恒
弾性合金を製造する。この場合、冷間加工は加工
率10〜90％の範囲で施され、時効処理条件として
は、例えば200〜750℃で0.1〜100時間の加熱を行
なう。
〔実施例〕
次に、本発明の実施例を説明する。
実施例 １
下記表に示す成分組成の合金を高周波真空溶解
法により製造し、得られたインゴツトを熱間加工
して厚さ２mmの板材とした。次いで、この板材を
1000℃×１時間、加熱保持した後、水焼入れを行
ない、更に50％の冷間圧延を行なつて厚さ１mmと
した。
得られた板材を試験素材として時効処理後、恒
弾性特性と引張強さを測定した。その結果を、同
表に併記した。恒弾性特性は、熱弾性係数を用い
て評価し、測定は１×10×100mmに切り出した試
験片の固有振動数（横振動法）の周波数の温度依
存性で評価した。この測定値をベースにして弾性
率（ヤング率Ｅ）を求め、温度による変化状態を
図示した特性図中に曲線ａで示した。
また、弾性率の温度変化依存性（変化率）を
ｅ，熱膨張係数の温度依存性（変化率）をαとす
ると、熱弾性係数＝ｅ×αで表わされる。この熱
弾性係数は恒弾性特性を評価する指標として用い
られ、これが零に近い程、恒弾性特性に優れてい
るが、本実施例１の合金はこの熱弾性係数が常温
（20℃）から130℃の間で８×10-6〔１／℃〕と極
めて低い値を示した。
実施例 ２〜９
下記表に示す成分組成の合金を実施例１と同様
な方法で製造し、得られた板材から試験片を切り
出し、恒弾性特性度範囲と引張強さを測定した。
その結果を同表に併記した。なお、表中には本発
明合金の成分組成からはずれる合金を比較例１〜
３として併記し、かつ従来合金についても従来例
として併記した。従来例に合金については、弾性
率の温度依存性を図示の特性図中に曲線ｂで示し
た。
[Technical Field of the Invention] The present invention relates to a constant modulus alloy whose modulus of elasticity has very little temperature dependence and is mainly applied to precision instruments. [Technical background of the invention and its problems] In general, constant elastic alloys are used for precision parts such as torque indicators, clock measurement springs, precision bellows, absolute pressure gauges, flow meters, industrial pressure gauges, Bourdon tubes, etc. It is widely used as a material for structural parts or devices that do not want the elastic modulus to change due to temperature changes, such as vibrating body materials such as tuning fork sound pieces and oscillators. Conventionally, the Fe-Ni-based Elinvar alloy has been well-known as the above-mentioned constant modulus alloy, but this material must be used in a cold-worked state, and the cold working conditions do not affect the constant modulus properties or mechanical properties. The drawback was that it was greatly influenced. For this reason, in recent years Fe−Ni−Cr−Ti
-Al-based precipitated constant modulus alloys have come into widespread use. This precipitated constant modulus alloy is
By selecting cold working and heat treatment conditions, it is possible to reduce the thermoelastic coefficient (TEC), which is an index for evaluating constant elastic properties, to zero relatively easily, and it also has excellent strength properties. This shows that. However, the constant elastic properties of this precipitated constant elastic alloy can usually only be maintained up to about 70 to 80°C, which has a big limit when used in a high-temperature atmosphere, and the range of its application has also been limited. [Object of the invention] The present invention was made in view of the above circumstances, and it significantly improves the constant elasticity properties to 130°C or higher, and
The purpose of this invention is to provide a constant modulus alloy that has excellent properties equivalent to or superior to conventional precipitated constant modulus alloys in terms of strength. [Summary of the invention] The present invention uses nickel (Ni) 40.0 to 44.5 in weight%.
%, chromium (Cr) 4.0-6.5%, titanium (Ti) 0.5
~1.9%, aluminum (Al) 0.1~1.0%, zirconium (Zr) 0.2~2.0%, balance iron (Fe) and incidental impurities, and the first invention further comprises molybdenum (Mo) and niobium (Nb). The second invention is to add 0.1 to 5.5% of one or more metals of tantalum (Ta) and tungsten (W), and to heat it in a temperature range of 20°C to at least 130°C. It has constant elastic properties with an elastic modulus of ±20×10 -6 [1/°C]. Next, the effect of each component constituting the constant modulus alloy of the present invention and the reason for limiting the amount added thereof will be explained. Nickel (Ni) is the most effective element for maintaining constant elastic properties, and its addition amount is 40.0%.
If it is less than or exceeds 44.5%, effective constant elastic properties cannot be obtained. Like nickel, chromium (Cr) is an effective element for maintaining constant elastic properties, and if the amount added is less than 4.0% or more than 6.5%, sufficient constant elastic properties cannot be obtained. Addition of chromium is also effective in improving the corrosion resistance of the alloy. Titanium (Ti) is an element that precipitates during aging treatment and is effective in improving alloy strength. If the amount added is less than 0.5%, sufficient strength improvement cannot be obtained.
On the other hand, if it exceeds 1.99%, the constant elastic properties will deteriorate. Aluminum (Al), like titanium, is an effective element for improving alloy strength, and if the amount added is less than 0.0, sufficient strength improvement cannot be achieved.
On the other hand, if it exceeds 1.0%, the constant elastic properties will deteriorate. Zirconium (Zr) contributes to strength improvement when combined with titanium and aluminum. If the amount of zirconium added is less than 0.2%, sufficient strength improvement cannot be achieved, whereas if it exceeds 2.0%, the constant elastic properties will deteriorate. Furthermore, the amounts of molybdenum (Mo), niobium (Nb), tantalum (Ta), and tungsten (W)
By specifying the amount in the range of 0.1 to 5.5%, it is possible to improve the mechanical properties of the alloy without deteriorating the constant modulus properties even if it is used alone or in combination of two or more. Next, a method for manufacturing the constant modulus alloy of the present invention will be briefly explained. First, it is melted into a predetermined alloy composition by induction melting or the like in a vacuum or an inert gas atmosphere, and then processed into a predetermined shape by hot working. Furthermore, after performing cold working to form a predetermined shape, aging treatment is performed to produce a constant modulus alloy. In this case, the cold working is performed at a working rate of 10 to 90%, and the aging treatment conditions include, for example, heating at 200 to 750° C. for 0.1 to 100 hours. [Example] Next, an example of the present invention will be described. Example 1 An alloy having the composition shown in the table below was manufactured by a high frequency vacuum melting method, and the obtained ingot was hot worked into a plate material with a thickness of 2 mm. Next, this plate material
After heating and holding at 1000°C for 1 hour, water quenching was performed, and further cold rolling was performed by 50% to give a thickness of 1 mm. The obtained plate material was used as a test material and after aging treatment, constant elastic properties and tensile strength were measured. The results are also listed in the same table. The constant elastic properties were evaluated using the thermoelastic coefficient, and the measurements were evaluated based on the temperature dependence of the frequency of the natural frequency (transverse vibration method) of a test piece cut out to 1 x 10 x 100 mm. The elastic modulus (Young's modulus E) was determined based on this measured value, and is shown as a curve a in the characteristic diagram illustrating the state of change due to temperature. Furthermore, if the temperature change dependence (rate of change) of the elastic modulus is e and the temperature dependence (change rate) of the thermal expansion coefficient is α, then the thermoelastic coefficient is expressed as e×α. This thermoelastic coefficient is used as an index to evaluate the constant elasticity properties, and the closer it is to zero, the better the constant elasticity properties are.The alloy of Example 1 has a thermoelastic coefficient of 130% from room temperature (20°C). It showed an extremely low value of 8×10 -6 [1/°C] between Examples 2 to 9 Alloys having the compositions shown in the table below were manufactured in the same manner as in Example 1, test pieces were cut from the obtained plates, and the range of constant elastic properties and tensile strength were measured.
The results are also listed in the same table. In addition, in the table, alloys that deviate from the composition of the present invention alloy are shown in Comparative Examples 1 to 1.
3, and the conventional alloys are also listed as conventional examples. Regarding the conventional alloy, the temperature dependence of the elastic modulus is shown by curve b in the illustrated characteristic diagram.
以上詳述した如く、本発明によれば恒弾性特性
を130℃以上まで大巾に向上させると共に、強度
的にも従来の析出形恒弾性合金と同等以上の優れ
た特性を有し、応用範囲の広い恒弾性合金を提供
できる。
As detailed above, according to the present invention, the constant modulus properties are greatly improved up to 130°C or higher, and the strength is also superior to that of conventional precipitated constant modulus alloys. We can offer a wide range of constant modulus alloys.
図面は本発明合金と従来合金の弾性率の温度変
化依存性を示す特性図である。
The drawing is a characteristic diagram showing the temperature change dependence of the elastic modulus of the alloy of the present invention and the conventional alloy.
Claims (1)
ム（Cr）4.0〜6.5％、チタン（Ti）0.5〜1.9％、
アルミニウム（Al）0.1〜1.0％、ジルコニウム
（Zr）0.2〜2.0％、残部鉄（Fe）と附随的不純物
よりなり、20℃から130℃の温度範囲で熱弾性係
数が±20×10-6［１／℃］以内の恒弾性特性を有
することを特徴とする恒弾性合金。 ２ 重量％でニツケル（Ni）40.0〜44.5％、クロ
ム（Cr）4.0〜6.5％チタン（Ti）0.5〜1.9％、ア
ルミニウム（Al）0.1〜1.0％、ジルコニウム
（Zr）0.2〜2.0％、モリブデン（Mo）、ニオブ
（Nb）、タンタル（Ta）及びタングステン（Ｗ）
のうちの１種又は２種以上の金属0.1〜5.5％、残
部鉄（Fe）と附随的不純物よりなり、20℃から
130℃の温度範囲で熱断性係数が±20×10-6［１／
℃］以内の恒弾性特性を有することを特徴とする
恒弾性合金。[Claims] 1. Nickel (Ni) 40.0 to 44.5%, chromium (Cr) 4.0 to 6.5%, titanium (Ti) 0.5 to 1.9%,
Consisting of 0.1~1.0% aluminum (Al), 0.2~2.0% zirconium (Zr), and the balance iron (Fe) and incidental impurities, the thermoelastic coefficient is ±20×10 -6 in the temperature range from 20℃ to 130℃ [ 1/°C]. 2 By weight, nickel (Ni) 40.0-44.5%, chromium (Cr) 4.0-6.5%, titanium (Ti) 0.5-1.9%, aluminum (Al) 0.1-1.0%, zirconium (Zr) 0.2-2.0%, molybdenum ( Mo), niobium (Nb), tantalum (Ta) and tungsten (W)
Consisting of 0.1 to 5.5% of one or more of the following metals, the balance being iron (Fe) and incidental impurities, from 20℃
Thermal insulation coefficient is ±20×10 -6 [1/
A constant modulus alloy characterized by having constant modulus properties within ℃].
Priority Applications (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5357083A JPS59179763A (en) | 1983-03-31 | 1983-03-31 | Constant-modulus alloy |
| US06/578,702 US4517158A (en) | 1983-03-31 | 1984-02-09 | Alloy with constant modulus of elasticity |
| DE8484300843T DE3460583D1 (en) | 1983-03-31 | 1984-02-10 | An alloy with constant modulus of elasticity |
| EP84300843A EP0122689B1 (en) | 1983-03-31 | 1984-02-10 | An alloy with constant modulus of elasticity |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5357083A JPS59179763A (en) | 1983-03-31 | 1983-03-31 | Constant-modulus alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS59179763A JPS59179763A (en) | 1984-10-12 |
| JPH0359974B2 true JPH0359974B2 (en) | 1991-09-12 |
Family
ID=12946486
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP5357083A Granted JPS59179763A (en) | 1983-03-31 | 1983-03-31 | Constant-modulus alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS59179763A (en) |
-
1983
- 1983-03-31 JP JP5357083A patent/JPS59179763A/en active Granted
Also Published As
| Publication number | Publication date |
|---|---|
| JPS59179763A (en) | 1984-10-12 |
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| JPS6075553A (en) | Diaphragm |