JPH0321623B2 - - Google Patents
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- JPH0321623B2 JPH0321623B2 JP54038312A JP3831279A JPH0321623B2 JP H0321623 B2 JPH0321623 B2 JP H0321623B2 JP 54038312 A JP54038312 A JP 54038312A JP 3831279 A JP3831279 A JP 3831279A JP H0321623 B2 JPH0321623 B2 JP H0321623B2
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- thermal expansion
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- amount
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Description
本発明は、200〜300℃の温度範囲における平均
熱膨脹係数が10×10-6／℃以下であつて、引張り
強さが100Kg／mm2以上である高強度低熱膨脹合金
に関する。
The present invention relates to a high-strength, low-thermal-expansion alloy having an average coefficient of thermal expansion of 10×10 -6 /°C or less in a temperature range of 200 to 300°C and a tensile strength of 100 Kg/mm 2 or more.
【従来の技術】
最近、通信用や計測用の精密機器の部品を製作
するため、あるいは機器の小型化による使用温度
の上昇に対応するため、300℃以上の温度まで高
精度を維持する、すなわち変形量の小さい構造材
料が要求されている。この種の構造材料としての
機能をはたすには、低熱膨脹率であると同時に、
高強度であることが必須条件となる。
本発明者らは、各種の用途例を調査し、200〜
300℃の平均熱膨脹係数が10×10-6／℃以下であ
り、かつ常温引張り強さが100Kg／mm2以上であれ
ば、通常の使用に耐えうると判断した。
そこで、在来のインバー合金（36Ni−Fe、引
張り強さ60Kg／mm2）を基本組成にして、これに対
する添加元素や熱履歴、さらには加工の影響を詳
細に調査した結果、Ｃ：0.1％超過〜0.3％未満、
Ni：35.0〜50.0％に加えて、Si、NnおよびCrの
１種または２種以上を（２種以上の場合は合計量
で）1.0％超過〜5.0％含有し、残余は実質的にFe
からなる合金に高度の冷間加工を施したものが、
上記の特性条件をみたし得ること、また、Niの
うち0.1〜8.0％の範囲の量を、CuまたはCuおよび
Coで置き換えるのが好ましいことを見出した。[Prior Art] Recently, in order to manufacture parts for precision equipment for communication and measurement, or to cope with the rise in operating temperatures due to miniaturization of equipment, high accuracy has been maintained up to temperatures of 300°C or higher. Structural materials with low deformation are required. In order to function as this type of structural material, it must have a low coefficient of thermal expansion and, at the same time,
High strength is an essential condition. The inventors investigated various application examples and found that 200 to 200
It was determined that if the average coefficient of thermal expansion at 300°C was 10×10 −6 /°C or less and the room temperature tensile strength was 100 Kg/mm 2 or more, it could withstand normal use. Therefore, we took a conventional Invar alloy (36Ni-Fe, tensile strength 60Kg/mm 2 ) as its basic composition and investigated in detail the effects of additive elements, thermal history, and processing, and found that C: 0.1% Excess ~ less than 0.3%,
Ni: In addition to 35.0 to 50.0%, it contains one or more of Si, Nn, and Cr (in the case of two or more types, the total amount) in excess of 1.0% to 5.0%, and the remainder is substantially Fe.
An alloy made of
The above characteristic conditions should be met, and the amount of Ni in the range of 0.1 to 8.0% should be Cu or Cu and
It has been found that it is preferable to replace it with Co.
本発明の目的は、上記した知見にもとづき、イ
ンバー合金よりも高い100Kg／mm2以上のレベルの
強度を有し、200〜300℃における平均熱膨脹係数
が10×10-6／℃以下である合金を提供することに
ある。
Based on the above-mentioned knowledge, the object of the present invention is to create an alloy that has a strength level of 100 Kg/mm 2 or more, which is higher than that of Invar alloy, and has an average coefficient of thermal expansion of 10 × 10 -6 /°C or less at 200 to 300°C. Our goal is to provide the following.
上記の目的を達成する本発明の高強度低熱膨脹
合金は、基本的には、Ｃ：0.1％超過〜0.3％未満
およびCu：0.1〜8.0％を含有し、（Ni＋Cu）：35.0
〜50.0％となる量のNiを含有するとともに、Si、
MnおよびCrの１種または２種以上を（２種以上
の場合は合計量で）1.0％超過〜5.0％含有し、残
余が実質的にFeからなる組成の合金に対し、減
面率50％以上の冷間加工を施してなり、200〜300
℃の平均熱膨脹係数が10×10-6／℃以下、常温引
張り強さが100Kg／mm2以上である。
上記の基本組成に対して、Cuの一部をCoで置
き換えることができる。CoはCuと同様に熱膨脹
係数を近い値に安定させるはたらきがある。
上記組成の高強度低熱膨脹合金に対して、さら
にTi、Nb、Ｖ、Zr、Ta、Ｗ、Hf、Alの１種ま
たは２種以上を（２種以上の場合は合計量で）
4.5％以下含有させることもでき、これは300℃付
近までのヒートサイクルにおける熱膨脹率を低く
保つのに効果的である。
The high-strength, low-thermal-expansion alloy of the present invention that achieves the above objects basically contains C: more than 0.1% to less than 0.3%, Cu: 0.1 to 8.0%, and (Ni+Cu): 35.0%.
Contains Ni in an amount of ~50.0%, and also contains Si,
Area reduction rate of 50% for alloys containing one or more of Mn and Cr (in the case of two or more, the total amount) exceeding 1.0% to 5.0%, with the remainder essentially consisting of Fe. It has been subjected to cold working of more than 200~300
The average coefficient of thermal expansion in °C is 10×10 -6 /°C or less, and the room temperature tensile strength is 100 Kg/mm 2 or more. For the above basic composition, part of Cu can be replaced with Co. Like Cu, Co has the function of stabilizing the coefficient of thermal expansion to a similar value. In addition to the high-strength, low-thermal-expansion alloy with the above composition, one or more of Ti, Nb, V, Zr, Ta, W, Hf, and Al (in the case of two or more types, the total amount)
It can be contained in an amount of 4.5% or less, which is effective in keeping the coefficient of thermal expansion low during heat cycles up to around 300°C.
本発明の合金の組成を上記のように定めた理由
は、つぎのとおりである。
Ｃ：0.1％超過〜0.3％未満
固溶および加工硬化による材質強化に寄与す
る。100Kg／mm2以上の引張り強さを確保するには、
0.1％を超える添加を必要とする。一方、多すぎ
るとFe−Ni系合金本来の低熱膨脹特性を損うた
め、0.3％未満に止める。
CuまたはCu＋Co：0.1〜8.0％
これらの元素は、Fe−Ni系合金の磁気変態点
を高温側に移動させ、熱膨脹係数曲線を低Ni側
に移動させる効果をもつ。この効果は、0.1％以
上の添加により明確になる。しかし多量にすぎる
と、かえつて熱膨脹係数を上昇させるため、8.0
％以下に止める。合金の製品の中には、加工工程
の途中で、歪取り、焼鈍メツキ、窒化などの表面
処理が施されるものも少なくない。そうした熱履
歴によつて、強加工による熱膨脹係数の低減効果
が失なわれやすい。これに対しては、Cuまたは
CuおよびCoの導入が効果的である。
Ni：（Ni＋Cu）または（Ni＋Cu＋Co）が35.0〜
50.0％となる量
低い熱膨脹係数が得られる温度範囲はNi含有
量により変化し、200〜300℃での熱膨脹係数を10
×10-6／℃以下にするためには、Niを、（Ni＋
Cu）または（Ni＋Cu＋Co）が少なくとも35.0％
となる量含有させる必要がある。これより多くな
ると熱膨脹係数はいつたん低下したのち上昇に転
じ、50.0％以上になるとこのレベルを維持するこ
とが困難となる。
Si、Mn、Cr：１種または２種以上、２種以上の
場合は合計量で1.0％超過〜5.0％
これらの元素は、Fe−Ni系合金本来の熱膨脹
特性をあまり損うことなく固溶強化でき、さらに
冷間加工を施したときの加工硬化も大きく、材質
強化に貢献する。100Kg／mm2以上の高強度を確保
するためには少なくとも合計量が1.0％を超える
必要がある。しかし多すぎると200〜300℃の熱膨
脹係数が高くなり、10×10-6／℃以下の条件を維
持することが困難になる。
Ti、Nb、Ｖ、Zr、Ta、Ｗ、Hf、Al：１種また
は２種以上（２種以上の場合は合計量で）4.5
％以下
これらの元素は、300℃付近までのヒートサイ
クルにおける熱膨脹係数を低位に安定させる上で
有効であり、さらにそれ自体の固溶強化作用や時
効処理によつて強度を一層向上させるのに役立
つ。一方、多すぎると熱膨脹係数が高くなり、
200〜300℃において10×10-6／℃以下という条件
をみたすことが困難となる。
減面率50％以上の冷間加工：
このような強加工を施すことによつて、引張り
強度が向上する一方で、熱膨脹率も低くなるとい
う好結果が得られる。
本発明の合金に対して時効処理を施すと、低熱
膨脹特性を損なうことなく引張強さ、弾性限界お
よび疲労強さを効果的に向上させることができ
る。この時効処理は、上記の減面率50％以上の冷
間加工に続いて行なうとよい。
参考例 １
電解鉄、フエロニツケルなどの原料を真空誘導
炉で溶解して得た溶湯に、適量のSi、Mnまたは
Crを添加し、第１表に示す組成の合金の鋳塊を
製造した。
第１表において、No.１〜７はNi含有量を変化
させたグループであり、No.８〜18は（Si＋Mn＋
Cr）含有量を変化させたグループである。
上記の供試材を鍛造し、線材圧延して直径10mm
の線材とし、950℃で焼鈍後、減面率80％および
90％にまで伸線加工を行なつた。その伸線材から
熱膨脹試験片および引張り試験片を採取した。
熱膨脹係数は常温から300℃までの範囲で測定
し、200〜300℃の平均熱膨脹係数を求めた。その
結果と引張り試験の結果とを、Ni量および（Si
＋Mn＋Cr）量で整理し、その一部を、それぞれ
第１図および第２図に示した。
（減面率80％のものを●印、90％のものを○印で
示した）
第１図に見るように、熱膨脹係数はNi量に従
つて変化し、35％を超えると10×10-6／℃以下と
なるが、40％を超えると増加しはじめる。ただ
し、熱膨脹係数を最小とするNi量は、Si、Mnな
どの添加元素とその量や、冷間加工、熱履歴によ
つても若干変化する。
第２図において、（Si＋Mn＋Cr）量が与える
熱膨脹係数への影響には、データに若干のバラツ
キが見られるものの、添加量の増大につれて熱膨
脹係数は上昇し、同時に引張り強さも増大する。
The reason for determining the composition of the alloy of the present invention as described above is as follows. C: More than 0.1% to less than 0.3% Contributes to material strengthening through solid solution and work hardening. To ensure tensile strength of 100Kg/mm2 or more ,
Requires addition of more than 0.1%. On the other hand, if it is too large, it will impair the low thermal expansion characteristics inherent to Fe-Ni alloys, so it should be kept at less than 0.3%. Cu or Cu+Co: 0.1 to 8.0% These elements have the effect of moving the magnetic transformation point of the Fe-Ni alloy to the high temperature side and moving the thermal expansion coefficient curve to the low Ni side. This effect becomes clearer when 0.1% or more is added. However, if the amount is too large, it will increase the coefficient of thermal expansion, resulting in
Keep it below %. Many alloy products undergo surface treatments such as strain relief, annealing plating, and nitriding during the processing process. Due to such a thermal history, the effect of reducing the coefficient of thermal expansion due to heavy working is likely to be lost. For this, Cu or
Introduction of Cu and Co is effective. Ni: (Ni+Cu) or (Ni+Cu+Co) from 35.0
50.0% The temperature range in which a low thermal expansion coefficient can be obtained varies depending on the Ni content, and the thermal expansion coefficient at 200 to 300℃ is 10.
In order to reduce the temperature to below ×10 -6 /℃, Ni must be (Ni +
Cu) or (Ni+Cu+Co) is at least 35.0%
It is necessary to contain the amount such that When the amount exceeds this value, the thermal expansion coefficient decreases and then starts to increase, and when it exceeds 50.0%, it becomes difficult to maintain this level. Si, Mn, Cr: 1 type or 2 or more types, in the case of 2 or more types, the total amount exceeds 1.0% to 5.0% These elements can be dissolved in solid solution without significantly impairing the thermal expansion characteristics inherent to Fe-Ni alloys. It can be strengthened, and it also exhibits significant work hardening when subjected to cold working, which contributes to strengthening the material. In order to ensure high strength of 100Kg/mm 2 or more, the total amount must exceed at least 1.0%. However, if the amount is too large, the coefficient of thermal expansion at 200 to 300°C becomes high, making it difficult to maintain the condition of 10×10 -6 /°C or less. Ti, Nb, V, Zr, Ta, W, Hf, Al: 1 type or 2 or more types (if 2 or more types, total amount) 4.5
% or less These elements are effective in stabilizing the coefficient of thermal expansion at a low level during heat cycles up to around 300℃, and are also useful in further improving strength through their own solid solution strengthening action and aging treatment. . On the other hand, if it is too large, the coefficient of thermal expansion will increase,
It becomes difficult to satisfy the condition of 10×10 -6 /°C or less at 200 to 300°C. Cold working with an area reduction of 50% or more: By performing such strong working, good results can be obtained in that the tensile strength is improved and the coefficient of thermal expansion is also lowered. When the alloy of the present invention is subjected to aging treatment, the tensile strength, elastic limit and fatigue strength can be effectively improved without impairing the low thermal expansion properties. This aging treatment is preferably performed following the above-mentioned cold working with an area reduction rate of 50% or more. Reference example 1 An appropriate amount of Si, Mn or
Cr was added to produce an alloy ingot having the composition shown in Table 1. In Table 1, Nos. 1 to 7 are groups with different Ni contents, and Nos. 8 to 18 are (Si + Mn +
This is a group with varying Cr) content. The above sample material was forged and wire rolled to a diameter of 10 mm.
After annealing at 950℃, the area reduction rate is 80% and
Wire drawing processing was performed to 90%. A thermal expansion test piece and a tensile test piece were taken from the drawn wire material. The coefficient of thermal expansion was measured in the range from room temperature to 300°C, and the average coefficient of thermal expansion from 200 to 300°C was determined. The results and the results of the tensile test were compared to the amount of Ni and (Si
+Mn+Cr) amount, some of which are shown in Figures 1 and 2, respectively. (Those with an area reduction rate of 80% are marked ●, and those with a reduction rate of 90% are marked ○.) As shown in Figure 1, the coefficient of thermal expansion changes according to the amount of Ni, and when it exceeds 35%, it becomes 10 × 10. It is below -6 /℃, but starts to increase when it exceeds 40%. However, the amount of Ni that minimizes the coefficient of thermal expansion varies slightly depending on the additional elements such as Si and Mn and their amounts, cold working, and thermal history. In Figure 2, although there is some variation in the data regarding the influence of the amount of (Si + Mn + Cr) on the coefficient of thermal expansion, as the amount added increases, the coefficient of thermal expansion increases, and at the same time, the tensile strength also increases.
【表】
参考例 ２
電解鉄、フエロニツケルなどの原料を真空誘導
炉で溶解して得た溶湯に、適量のSi、Mn、Ｃの
ほかTi、Nbなどを単独または複合添加し、第２
表に示す組成の合金の鋳塊を製造した。
これらの供試材から、実施例１と同様の鍛造、
線材圧延、焼鈍および減面率90％の伸線加工を行
なつた。得られた伸線材、およびそれに300℃×
１時間の時効処理を施したものから、引張り試験
片および熱膨脹試験片を採取して試験に供した。
その結果を（Ti＋Nb…Al）量で整理して、第
３図に示す。（○印は線引材、●印は時効材）
同図に見るとおり、上記元素の添加量が増大す
るにつれて熱膨脹係数はやや増大する傾向がある
ものの、4.5％付近までは10×10-6／℃以下の条
件を満足させることができる。
また、伸線材にくらべ、300℃時効材では上記
元素の添加効果が大きい。このことは、無添加の
No.19は、一度300℃付近まで昇温すると冷間（線
引き）加工による低熱膨脹化の効果が低減し、熱
膨脹係数がかなり高くなることをみれば明らかで
ある。
上記元素の添加量の増大は、それに対応して引
張り強さを漸増させ、その効果はとくに時効材で
著しい。[Table] Reference Example 2 To the molten metal obtained by melting raw materials such as electrolytic iron and ferronic acid in a vacuum induction furnace, an appropriate amount of Si, Mn, and C, as well as Ti and Nb, etc. are added singly or in combination, and the second
An alloy ingot having the composition shown in the table was manufactured. From these test materials, forging similar to Example 1,
Wire rolling, annealing, and wire drawing with an area reduction rate of 90% were performed. The obtained wire drawing material and it were heated at 300℃
A tensile test piece and a thermal expansion test piece were taken from those subjected to the aging treatment for 1 hour and used for testing. The results are summarized by the amount of (Ti + Nb...Al) and are shown in Figure 3. (○ marks are wire-drawn materials, ● marks are aged materials) As seen in the figure, as the amount of the above elements added increases, the thermal expansion coefficient tends to increase slightly, but up to around 4.5%, the coefficient of thermal expansion is 10 × 10 -6 /°C or less can be satisfied. Furthermore, compared to drawn wire material, the effect of adding the above elements is greater in 300°C aged material. This means that additive-free
For No. 19, it is clear that once the temperature is raised to around 300°C, the effect of low thermal expansion due to cold (wire drawing) processing decreases, and the coefficient of thermal expansion becomes considerably high. Increasing the amount of the above-mentioned elements added gradually increases the tensile strength, and the effect is particularly pronounced in aged materials.
【表】
実施例 １
上記の参考例１および２によつて、アンバー合
金における各種添加元素、冷間加工および時効処
理が熱膨脹率および強度に及ぼす影響が明らかに
なつたので、次は、本発明に従つて、さらにCu
またはCuおよびCoを含有させ、第３表に示す組
成の合金の鋳塊を製造した。
それらの鋳塊から、参考例２と同様の工程をへ
て伸線材を得、引張り試験片および熱膨脹試験片
を採取して試験に供した。
その結果を（Co＋Cu）量で整理して、第４図
に示す。
図に見るとおり、CuおよびCoを含有すること
によつて熱膨脹係数が低くなるから、Niの一部
をCoおよびCuで置換することは有用である。し
かし、CuまたはCu＋Coの置換量があまり多くな
ると、熱膨脹係数を低める効果が減じ、またコス
ト的にも不利となる。[Table] Example 1 The above-mentioned Reference Examples 1 and 2 clarified the effects of various additive elements, cold working, and aging treatment on the coefficient of thermal expansion and strength of the amber alloy. According to further Cu
Alternatively, alloy ingots containing Cu and Co and having the compositions shown in Table 3 were manufactured. From these ingots, drawn wire materials were obtained through the same steps as in Reference Example 2, and tensile test pieces and thermal expansion test pieces were taken and used for testing. The results are shown in Figure 4, organized by the amount of (Co+Cu). As shown in the figure, it is useful to partially replace Ni with Co and Cu because the inclusion of Cu and Co lowers the coefficient of thermal expansion. However, if the substitution amount of Cu or Cu+Co is too large, the effect of lowering the coefficient of thermal expansion will be reduced and it will also be disadvantageous in terms of cost.
【表】
実施例 ２
第４図に示す組成の合金の鋳塊を製造し、参考
例２と同様にして伸線材から試験片をつくり、引
張強度および熱膨脹率を測定した。
その結果を、第４表にあわせて示す。[Table] Example 2 An alloy ingot having the composition shown in FIG. 4 was manufactured, and a test piece was made from the drawn wire material in the same manner as in Reference Example 2, and the tensile strength and coefficient of thermal expansion were measured. The results are also shown in Table 4.
【表】【table】
本発明の合金は、インバー合金を改良した組成
の合金に冷間の強加工を組み合わせることによつ
て、100Kg／mm2以上の高強度を付与し、かつ200〜
300℃の高温度領域においても10×10-6／℃以下
の低熱膨脹係数を実現したものである。
従つて本発明の合金は、高温領域で使用する精
密機器の部品の製造に好適である。
The alloy of the present invention has a high strength of 100 kg/mm 2 or more and a strength of 200 kg/mm 2 or more by combining an alloy with an improved composition of Invar alloy and cold working.
It has achieved a low thermal expansion coefficient of 10×10 -6 /°C or less even in the high temperature range of 300°C. Therefore, the alloy of the present invention is suitable for manufacturing parts of precision equipment used in high-temperature regions.
第１図ないし第３図は、いずれも本発明に対す
る参考例のデータを掲げたグラフであつて、第１
図は熱膨脹係数および引張り強度に対するNi量
の影響、第２図は（Si＋Mn＋Cr）量の影響、そ
して第３図は（Ti＋Nb＋Ｖ＋Zr＋Ta＋Ｗ＋Hf
＋Al）量の影響、をそれぞれ示す。第４図は本
発明の実施例のデータを掲げたグラフであつて、
第１図ないし第３図と同様に、熱膨脹係数および
引張り強度に対する（Cu＋Co）量の影響を示す。
1 to 3 are graphs showing data of reference examples for the present invention.
Figure 2 shows the effect of Ni content on thermal expansion coefficient and tensile strength, Figure 2 shows the effect of (Si + Mn + Cr) content, and Figure 3 shows the effect of (Ti + Nb + V + Zr + Ta + W + Hf).
+Al) amount influence. FIG. 4 is a graph showing data of an example of the present invention,
Similar to FIGS. 1 to 3, the influence of the amount of (Cu+Co) on the coefficient of thermal expansion and tensile strength is shown.
Claims (1)
8.0％を含有し、（Ni＋Cu）：35.0〜50.0％となる
量のNiを含有するとともに、Si、MnおよびCrの
１種または２種以上を（２種以上の場合は合計量
で）1.0％超過〜5.0％含有し、残余が実質的にFe
からなる組成の合金に対し、減面率50％以上の冷
間加工を施してなり、200〜300℃の平均熱膨脹係
数が10×10-6／℃以下、常温引張強さが100Kg／
mm2以上である高強度低熱膨脹合金。 ２ Ｃ：0.1％超過〜0.3％未満ならびにCuおよび
Co（合計）：0.1〜8.0％を含有し、（Ni＋Cu＋
Co）：35.0〜50.0％となる量のNiを含有するとと
もに、Si、MnおよびCrの１種または２種以上を
1.0％超過〜5.0％含有し、残余が実質的にFeから
なる組成の合金に対し、減面率50％以上の冷間加
工を施してなり、200〜300℃の平均熱膨脹係数が
10×10-6／℃以下、常温引張り強さが100Kg／mm2
以上である高強度低熱膨脹合金。 ３ Ｃ：0.1％超過〜0.3％未満およびCu：0.1〜
8.0％を含有し、（Ni＋Cu）：35.0〜50.0％となる
量のNiを含有するとともに、Si、MnおよびCrの
１種または２種以上を（２種以上の場合は合計量
で）1.0％超過〜5.0％含有し、さらにTi、Nb、
Ｖ、Zr、Ta、Ｗ、HfおよびAlの１種または２種
以上を（２種以上の場合は合計量で）4.5％以下
含有し、残余が実質的にFeからなる組成の合金
に対し、減面率50％以上の冷間加工を施してな
り、200〜300℃の平均熱膨脹係数が10×10-6／℃
以下、常温引張り強さが100Kg／mm2以上である高
強低度熱膨脹合金。[Claims] 1 C: more than 0.1% to less than 0.3% and Cu: 0.1 to less
Contains 8.0%, (Ni + Cu): 35.0 to 50.0%, and contains one or more of Si, Mn, and Cr (in the case of two or more types, the total amount) is 1.0%. Contains ~5.0% in excess, with the remainder essentially Fe
It is made by cold-working an alloy with a composition of
High strength low thermal expansion alloy that is larger than mm2 . 2 C: more than 0.1% to less than 0.3% and Cu and
Co (total): Contains 0.1 to 8.0%, (Ni + Cu +
Co): Contains 35.0 to 50.0% of Ni, and also contains one or more of Si, Mn, and Cr.
An alloy containing over 1.0% to 5.0%, with the remainder essentially consisting of Fe, is subjected to cold working with an area reduction rate of 50% or more, and has an average coefficient of thermal expansion of 200 to 300℃.
10×10 -6 /℃ or less, room temperature tensile strength 100Kg/mm 2
High strength low thermal expansion alloy. 3 C: more than 0.1% to less than 0.3% and Cu: 0.1 to
Contains 8.0%, (Ni + Cu): 35.0 to 50.0%, and contains one or more of Si, Mn, and Cr (in the case of two or more types, the total amount) is 1.0%. Contains ~5.0% in excess, and further contains Ti, Nb,
For alloys containing 4.5% or less of one or more of V, Zr, Ta, W, Hf and Al (in the case of two or more, the total amount), with the remainder essentially consisting of Fe, It is cold-worked with an area reduction of 50% or more, and the average coefficient of thermal expansion at 200 to 300℃ is 10×10 -6 /℃.
The following are high-strength, low-temperature expansion alloys with room temperature tensile strength of 100 Kg/mm 2 or more.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3831279A JPS55131155A (en) | 1979-04-02 | 1979-04-02 | High strength low thermal expansion alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3831279A JPS55131155A (en) | 1979-04-02 | 1979-04-02 | High strength low thermal expansion alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS55131155A JPS55131155A (en) | 1980-10-11 |
| JPH0321623B2 true JPH0321623B2 (en) | 1991-03-25 |
Family
ID=12521769
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP3831279A Granted JPS55131155A (en) | 1979-04-02 | 1979-04-02 | High strength low thermal expansion alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS55131155A (en) |
Families Citing this family (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS55152156A (en) * | 1979-05-14 | 1980-11-27 | Toshiba Corp | Low expansion alloy |
| JPS57207160A (en) * | 1981-06-17 | 1982-12-18 | Kawasaki Steel Corp | Low thermal expansion invar type fe-ni alloy with superior rust resistance |
| JPS58141366A (en) * | 1982-02-16 | 1983-08-22 | Toshiba Corp | Parts in tube |
| US4517158A (en) * | 1983-03-31 | 1985-05-14 | Tokyo Shibaura Denki Kabushiki Kaisha | Alloy with constant modulus of elasticity |
| JPS61113747A (en) * | 1984-11-07 | 1986-05-31 | Nippon Mining Co Ltd | Material for shadow mask |
| JPS61149461A (en) * | 1984-12-25 | 1986-07-08 | Nippon Mining Co Ltd | Shadow mask material and shadow mask |
| JPH02298236A (en) * | 1989-05-12 | 1990-12-10 | Shinichi Enomoto | Low thermal expansion alloy |
| JPH0625395B2 (en) * | 1989-06-26 | 1994-04-06 | 日立金属株式会社 | High-strength leadframe material and manufacturing method thereof |
| US5246511A (en) * | 1990-05-14 | 1993-09-21 | Hitachi Metals, Ltd. | High-strength lead frame material and method of producing same |
| US5147470A (en) * | 1990-12-25 | 1992-09-15 | Hitachi Metals, Ltd. | High strength lead frame material and method of producing the same |
| US6221183B1 (en) | 1992-11-16 | 2001-04-24 | Hitachi Metals, Ltd. | High-strength and low-thermal-expansion alloy, wire of the alloy and method of manufacturing the alloy wire |
| JP4578847B2 (en) * | 2004-04-09 | 2010-11-10 | 伊藤鉄工株式会社 | Low thermal expansion cast iron |
| JP6634912B2 (en) * | 2016-03-22 | 2020-01-22 | 日本製鉄株式会社 | Low thermal expansion alloy |
Family Cites Families (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB1410732A (en) * | 1973-05-04 | 1975-10-22 | Int Nickel Ltd | Low expansion alloys |
| JPS549569B2 (en) * | 1972-02-17 | 1979-04-25 | ||
| GB1401259A (en) * | 1973-05-04 | 1975-07-16 | Int Nickel Ltd | Low expansion alloys |
| GB1411693A (en) * | 1973-05-04 | 1975-10-29 | Int Nickel Ltd | Low expansion alloys |
| JPS5152922A (en) * | 1974-11-06 | 1976-05-11 | Nisshin Steel Co Ltd | Netsukankakoseino sugureta ko niife gokin |
| JPS5597453A (en) * | 1979-01-18 | 1980-07-24 | Daido Steel Co Ltd | Alloy with high strength and low thermal expansion |
| JPS55122855A (en) * | 1979-03-12 | 1980-09-20 | Daido Steel Co Ltd | High strength low thermal expansion alloy |
-
1979
- 1979-04-02 JP JP3831279A patent/JPS55131155A/en active Granted
Also Published As
| Publication number | Publication date |
|---|---|
| JPS55131155A (en) | 1980-10-11 |
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