JPH07113143B2 - Method for producing high strength copper alloy - Google Patents
Method for producing high strength copper alloyInfo
- Publication number
- JPH07113143B2 JPH07113143B2 JP62067665A JP6766587A JPH07113143B2 JP H07113143 B2 JPH07113143 B2 JP H07113143B2 JP 62067665 A JP62067665 A JP 62067665A JP 6766587 A JP6766587 A JP 6766587A JP H07113143 B2 JPH07113143 B2 JP H07113143B2
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- Japan
- Prior art keywords
- alloy
- copper alloy
- weight
- strength copper
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Description
【発明の詳細な説明】 〔産業上の利用分野〕 この発明は,特にスイツチ,リレー関係の繰返し応力が
負荷される用途に適した疲れ特性の良好な高強度銅合金
の製造方法に関するものである。TECHNICAL FIELD The present invention relates to a method for producing a high-strength copper alloy having good fatigue characteristics, which is particularly suitable for applications in which cyclic stress related to switches and relays is applied. .
従来,市場で一般的に使用されている高強度銅合金とし
て代表的なものに,例えば雑誌:伸銅技術研究会誌Vol.
9(1970)P109〜P116に示されているC1720合金(ベリリ
ウム銅合金)があるが,この合金は資源希少で安定供給
を受けにくい高価なBeを含有するためにコスト面で問題
がある。一方,安価なバネ材としてはCu中にSnと微量の
Pを含有するリン青銅系の合金があり,その機械的特性
は,例えば刊行物:ASTM Spec.Tech.Pub.No.183(1956)
にも示されているように,Sn含有量の増加につれて増大
する傾向を有する。しかし,Sn量が多くなると,硬くて
脆い展延性の乏しい化合物相,例えばδ,β相等の晶出
やSnの逆偏析現象の出現により,加工性が極端に悪化す
るため,圧延等の冷間加工が不可能で,リン青銅鋳物と
してしか利用できない難点がある。従つて現在,この合
金系でバネ材として実使用されている合金のSn含有量の
最大は9%程度どまりである。このためにC1720合金と
の特性差が大きく,この間を埋める合金の出現が要望さ
れている。A typical example of high-strength copper alloys that have been commonly used in the market, for example, is the Journal of Copper and Copper Technology, Vol.
There is a C1720 alloy (beryllium copper alloy) shown in 9 (1970) P109 to P116, but this alloy has a problem in terms of cost because it contains expensive Be, which is a scarce resource and does not easily receive a stable supply. On the other hand, as an inexpensive spring material, there is a phosphor bronze-based alloy containing Sn and a small amount of P in Cu, and its mechanical properties are, for example, published: ASTM Spec.Tech.Pub.No.183 (1956).
As also shown, it has a tendency to increase with increasing Sn content. However, when the Sn content is large, the workability becomes extremely poor due to the crystallization of hard and brittle compound phases with poor ductility, such as the δ and β phases, and the appearance of the reverse segregation phenomenon of Sn. It cannot be processed and has the drawback that it can only be used as a phosphor bronze casting. Therefore, the maximum Sn content of the alloy currently used as a spring material in this alloy system is only about 9%. For this reason, there is a large difference in characteristics from the C1720 alloy, and the emergence of an alloy that fills this gap is desired.
従来,資源希少で安定供給を受けにくい高価なBeを使用
せずに,安定供給可能なリン青銅系合金で機械的特性,
加工性に優れ,バネ材としての十分な特性を有するもの
が得られないという問題点があつた。Conventionally, phosphor bronze-based alloys that can be stably supplied without using expensive Be, which is a scarce resource and difficult to receive a stable supply, have mechanical properties,
There was a problem in that it was not possible to obtain a material with excellent workability and sufficient properties as a spring material.
この発明は上記のような問題点を解消するためになされ
たもので,資源希少で安定供給を受けにくいBeを使用せ
ずに,リン青銅系合金の組織と冷間加工性の改善を図
り,バネ材として十分な特性を有する高強度銅合金を得
ることを目的とする。The present invention has been made to solve the above problems, and aims to improve the structure and cold workability of a phosphor bronze alloy without using Be, which is a resource scarce and does not easily receive a stable supply, The purpose is to obtain a high-strength copper alloy having sufficient properties as a spring material.
この発明の高強度銅合金は,12重量%を越え20重量%以
下のSnと0.01〜0.5重量%のPを含有し,残部Cuからな
る溶湯金属を,102℃/sec以上105℃/sec未満の冷却速度
で急冷凝固させて製造するものである。The high-strength copper alloy of the present invention contains Sn in an amount of more than 12% by weight and 20% by weight or less and 0.01 to 0.5% by weight of P, and the balance of the molten metal consisting of Cu is 10 2 ℃ / sec or more and 10 5 ℃ / It is manufactured by rapid solidification at a cooling rate of less than sec.
合金の鋳塊製造時において溶湯を102℃/sec以上105℃/s
ec未満の冷却速度で急冷凝固することにより,逆偏析の
出現を抑制するとともに,化合物相を微細に且つ均一に
マトリツクス中に分散できるので,組織と冷間加工性の
改善が図れる。10 2 ℃ / sec or more 10 5 ℃ / s
By quenching and solidifying at a cooling rate less than ec, the occurrence of reverse segregation can be suppressed and the compound phase can be finely and uniformly dispersed in the matrix, improving the structure and cold workability.
以下にこの発明の実施例について説明する。 Examples of the present invention will be described below.
発明材は,直径200mmで内部水冷が可能な鋳鉄製双ロー
ルからなる実験用の急冷凝固設備を用いて作製した。製
造条件としては,(1)冷却ロールの回転数を10rpm,
(ii)ロールへの注湯温度はいずれも合金の融点から50
℃高目,(iii)ロールギヤツプは1mmに設定した。得ら
れた薄板鋳塊は厚さ1.8mm,巾100mmであつた。この鋳塊
では,従来の連続鋳造法やバツチ式鋳造に比べて早い10
2℃/sec以上105℃/sec未満の冷却速度で連続的に急冷凝
固させるため,デンドライト組織や逆偏析の出現が抑制
され,しかも化合物相が微細にマトリツクス中に均一に
分散した状態となつており,加工性は極めて良好であ
る。これらの鋳塊を均質化焼鈍なしで一気に板厚0.3mm
まで冷間圧延した後,500℃で1時間のキジ焼鈍に続いて
33%の冷間加工率にて0.2mmの板厚に仕上げた。次に250
℃で1時間の低温焼鈍処理を施し諸特性測定用の試料と
した。The invented material was produced using an experimental rapid solidification facility consisting of cast iron twin rolls with a diameter of 200 mm and capable of internal water cooling. The manufacturing conditions are (1) the rotation speed of the cooling roll is 10 rpm,
(Ii) The pouring temperature to the roll is 50 from the melting point of the alloy.
Higher at ℃, (iii) Roll gap was set to 1 mm. The obtained thin plate ingot had a thickness of 1.8 mm and a width of 100 mm. This ingot is faster than conventional continuous casting and batch casting.
The continuous rapid solidification at a cooling rate of 2 ° C / sec or more and less than 10 5 ° C / sec suppresses the appearance of dendrite structure and reverse segregation, and the compound phase is finely dispersed uniformly in the matrix. The workability is extremely good. The thickness of these ingots is 0.3 mm at a stretch without homogenizing and annealing.
Cold rolled to 500 ° C, followed by 1 hour pheasant annealing
Finished to a thickness of 0.2 mm with a cold working rate of 33%. Then 250
A low temperature annealing treatment was performed at 1 ° C. for 1 hour to obtain a sample for measuring various characteristics.
第1表は,この発明材と比較材の特性値をまとめて示し
たものである。Table 1 summarizes the characteristic values of the invention material and the comparative material.
これらの結果から明らかなように,12重量%を越えるSn
を含有するCu−Sn系合金をこの発明のように急冷凝固し
て製造することにより,冷間加工性が著しく改善され,
バネ材として適した高強度銅合金が得られることがわか
る。例えば,バネ材として一般的に広く実用されている
試料No.1のC5210合金(比較材,特開昭5−112324号な
ど)とその約2倍のSnを含有する試料No.3(本発明材)
の特性を比較すると,試料No.3の方が引張強さで約50
%,ばね限界値では約110%も増大している。一方,バ
ネ材として重視される疲れ特性についても改善効果が認
められ,繰返し数N=107回における疲れ強さで32kg f/
mm2の値が得られ,レベル的にはC5210合金とC1720合金
の中間位置にある。As is clear from these results, Sn exceeding 12 wt%
The cold workability is remarkably improved by producing a Cu-Sn alloy containing Cu by rapid solidification as in the present invention.
It can be seen that a high-strength copper alloy suitable as a spring material can be obtained. For example, the C5210 alloy of Sample No. 1 (comparative material, Japanese Patent Laid-Open No. 5-112324, etc.), which is generally widely used as a spring material, and Sample No. 3 containing about twice that amount of Sn (the present invention). Material)
Comparing the characteristics of Sample No. 3, the tensile strength of Sample No. 3 is about 50.
%, The spring limit value has increased by about 110%. On the other hand, improvement is also observed for the fatigue characteristics are important as a spring member, 32 kg in fatigue strength at the repetition rate N = 10 7 times f /
A value of mm 2 was obtained, and the level is at the intermediate position between the C5210 alloy and the C1720 alloy.
これらの機械的特性の向上は,従来品よりSn含有量を多
くし固溶硬化能と加工硬化能が増大したこと並びにマト
リツクス中に微細な化合物を均一に分散させることによ
る。特に,疲れ特性の向上については,マトリツクス中
に分散した微細な化合物が疲労クラツクの伝播を阻止す
るためと考えられる。Snの含有量としては12重量%以下
では機械的特性が不十分であり,20重量%以上では機械
的特性は向上するものの,C1720合金と比べてコストメリ
ツトが薄らぐとともに,加工性が低下するため,12重量
%を越え20重量%以下の範囲が望ましく,12.4〜20重量
%の範囲が好適である。またPの含有量としては0.01重
量%以下では実用上脱酸剤としての効果がなく,0.5重量
%以上含んでいても効果に変化はなく,電気伝導度を下
げないためには少ない方が良く,0.01〜0.5重量%の範囲
が良い。 The improvement of these mechanical properties is due to the fact that the Sn content is increased and the solid solution hardening ability and work hardening ability are increased compared with the conventional product, and the fine compound is uniformly dispersed in the matrix. In particular, the improvement of fatigue properties is considered to be due to the fact that fine compounds dispersed in the matrix prevent the propagation of fatigue cracks. If the Sn content is 12 wt% or less, the mechanical properties are insufficient, and if the Sn content is 20 wt% or more, the mechanical properties are improved, but the cost merit becomes thinner and the workability decreases as compared to the C1720 alloy. The range of more than 12% by weight and 20% by weight or less is desirable, and the range of 12.4 to 20% by weight is preferable. Further, if the P content is 0.01% by weight or less, there is practically no effect as a deoxidizer, and if it is 0.5% by weight or more, the effect does not change. The range of 0.01 to 0.5% by weight is preferable.
第2表は微量の添加元素による効果を示したものであ
る。Table 2 shows the effect of a small amount of additional element.
Cu−Sn−Pをベースにした試料No.4と比較した場合,試
料No.5の引張強さ,ばね限界値,疲れ強 さは,いずれもほとんど差が認められないことから,Mn,
Zn,Bはこれらの特性に悪影響を及ぼさず,脱酸剤として
有効であることを示している。但し,添加量が多くなる
ともろくなり,加工性や導電率への影響が現われるため
上限値を設定している。一方,No.6〜No.9の試料を比較
した場合,Ni,Fe,Co,Ti,Zrの添加元素は,結晶粒の微細
化,強度を上げるのに貢献し,特に疲れ特性の向上に対
し効果が認められ,その上限については成形加工性の点
から制限をした。これら微量元素の含有量は1.0重量%
以上含まれると導電率を下げるので,実用上合計で0.01
〜1.0重量%以下が望ましい。また各微量元素の含有量
は上述の点から鑑みて実用上下記範囲が望ましい。When compared with the sample No.4 based on Cu-Sn-P, the tensile strength, spring limit value and fatigue strength of sample No.5 were compared. Since there is almost no difference in either case, Mn,
Zn and B do not adversely affect these properties, indicating that they are effective as deoxidizers. However, the higher the amount added, the more brittle it becomes and the workability and conductivity are affected. Therefore, the upper limit is set. On the other hand, when comparing No.6 to No.9 samples, the additive elements of Ni, Fe, Co, Ti, and Zr contribute to the refinement of crystal grains and increase in strength, and especially to the improvement of fatigue properties. On the other hand, the effect was recognized, and the upper limit was limited in terms of moldability. The content of these trace elements is 1.0% by weight
If the above content is included, the conductivity will be reduced, so the total practical value is 0.01.
It is desirable to be 1.0% by weight or less. In view of the above, the content of each trace element is practically desirable within the following range.
Ni……0.01〜0.5重量% Zn……0.01〜0.35重量% Fe……0.01〜0.15重量% Ti……0.01〜0.5重量% B……0.001〜0.1重量% CO……0.01〜0.5重量% Mn……0.05〜0.4重量% Zr……0.01〜0.5重量% なお,溶湯金属の冷却速度は種々実験した結果,102℃/s
ec未満では鋳塊組織が従来の鋳造法によるものと変らず
良好な加工性が得られないため,また105℃/sec以上で
は,製造可能な板厚が極端に薄くなり過ぎて実用に供し
にくくなるため,102℃/sec以上105℃/sec未満の範囲が
良い。Ni …… 0.01 to 0.5 wt% Zn …… 0.01 to 0.35 wt% Fe …… 0.01 to 0.15 wt% Ti …… 0.01 to 0.5 wt% B …… 0.001 to 0.1 wt% CO …… 0.01 to 0.5 wt% Mn… … 0.05 ~ 0.4wt% Zr …… 0.01 ~ 0.5wt% The cooling rate of molten metal was 10 2 ℃ / s as a result of various experiments.
If it is less than ec, the ingot structure is the same as that obtained by the conventional casting method and good workability cannot be obtained. If it is 10 5 ° C / sec or more, the plate thickness that can be manufactured is too thin and it is put to practical use. Since it becomes difficult, a range of 10 2 ° C / sec or more and less than 10 5 ° C / sec is preferable.
また,参考までにこの発明合金に係る製造法はCu−Sn系
合金だけではなく,展延性の悪い化合物相が晶出し易く
難加工材として知られているNi−Be−Al,Cu−Ni−Mn,Cu
−Ti系合金等に適用しても同様の効果を奏するものであ
る。In addition, for reference, the manufacturing method according to the alloy of the present invention is not limited to Cu-Sn alloys, but Ni-Be-Al, Cu-Ni- which is known as a difficult-to-process material that easily crystallizes a compound phase with poor ductility Mn, Cu
The same effect can be obtained even when applied to a Ti-based alloy or the like.
以上のように,この発明によれば,12重量%を越え20重
量%以下のSnと0.01〜0.5重量%のPを含有し,残部Cu
からなる溶湯金属を,102℃/sec以上105℃/sec未満の冷
却速度で急冷凝固させて製造することにより,組織の冷
間加工性が著しく改善され,バネ材,例えばスイツチ,
リレー関係の繰返し応力が負荷される用途に適した安定
供給を受けられ安価で,耐疲労性に優れた高強度銅合金
が得られる効果がある。As described above, according to the present invention, Sn of more than 12 wt% and 20 wt% or less and 0.01 to 0.5 wt% of P are contained, and the balance Cu
By rapidly solidifying molten metal consisting of 10 2 ℃ / sec or more and less than 10 5 ℃ / sec, the cold workability of the structure is remarkably improved, and spring materials such as switches,
It has the effect that a stable supply suitable for applications in which relay-related repetitive stress is applied can be received, and a low-strength, high-strength copper alloy with excellent fatigue resistance can be obtained.
Claims (3)
0.5重量%のPを含有し,残部Cuからなる溶湯金属を,10
2℃/sec以上105℃/sec未満の冷却速度で急冷凝固させて
製造する高強度銅合金の製造方法。1. Sn of more than 12% by weight and 20% by weight or less and 0.01-
The molten metal containing 0.5% by weight of P and the balance of Cu was 10
A method for producing a high-strength copper alloy produced by rapid solidification at a cooling rate of 2 ° C / sec or more and less than 10 5 ° C / sec.
いる特許請求の範囲第1項記載の高強度銅合金の製造方
法。2. The method for producing a high-strength copper alloy according to claim 1, wherein the molten metal contains 12.4 to 20% by weight of Sn.
を少くとも一種以上あわせて0.01〜1.0重量%含有して
いる特許請求の範囲第1項または第2項記載の高強度銅
合金の製造方法。3. Molten metal is Ni, Zn, Fe, Ti, B, Co, Mn and Zr.
The method for producing a high-strength copper alloy according to claim 1 or 2, further comprising 0.01 to 1.0 wt% of at least one of them.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP62067665A JPH07113143B2 (en) | 1987-03-20 | 1987-03-20 | Method for producing high strength copper alloy |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP62067665A JPH07113143B2 (en) | 1987-03-20 | 1987-03-20 | Method for producing high strength copper alloy |
Publications (2)
Publication Number | Publication Date |
---|---|
JPS63235455A JPS63235455A (en) | 1988-09-30 |
JPH07113143B2 true JPH07113143B2 (en) | 1995-12-06 |
Family
ID=13351524
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP62067665A Expired - Lifetime JPH07113143B2 (en) | 1987-03-20 | 1987-03-20 | Method for producing high strength copper alloy |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPH07113143B2 (en) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
KR20220090355A (en) * | 2020-12-21 | 2022-06-29 | 한국재료연구원 | Copper-Tin alloy for hot rolling and method for manufacturing thereof |
Families Citing this family (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE19756815C2 (en) * | 1997-12-19 | 2003-01-09 | Wieland Werke Ag | Wrought copper alloy, process for producing a semi-finished product therefrom and its use |
DE19928330C2 (en) * | 1999-06-21 | 2003-01-16 | Wieland Werke Ag | Use of a tin-rich copper-tin-iron wrought alloy |
US6346215B1 (en) | 1997-12-19 | 2002-02-12 | Wieland-Werke Ag | Copper-tin alloys and uses thereof |
JP5116976B2 (en) * | 2006-02-10 | 2013-01-09 | 三菱伸銅株式会社 | Raw brass alloy for semi-fusion gold casting |
JP2007211324A (en) * | 2006-02-13 | 2007-08-23 | Sanbo Copper Alloy Co Ltd | Raw material phosphor bronze alloy for casting half-melted alloy |
JP2007211325A (en) * | 2006-02-13 | 2007-08-23 | Sanbo Copper Alloy Co Ltd | Raw material aluminum bronze alloy for casting half-melted alloy |
JP5156316B2 (en) * | 2007-09-26 | 2013-03-06 | Dowaメタルテック株式会社 | Cu-Sn-P copper alloy sheet, method for producing the same, and connector |
Citations (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS61143524A (en) * | 1984-12-14 | 1986-07-01 | Nippon Kokan Kk <Nkk> | Manufacture of sheet-shaped slab |
-
1987
- 1987-03-20 JP JP62067665A patent/JPH07113143B2/en not_active Expired - Lifetime
Patent Citations (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS61143524A (en) * | 1984-12-14 | 1986-07-01 | Nippon Kokan Kk <Nkk> | Manufacture of sheet-shaped slab |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
KR20220090355A (en) * | 2020-12-21 | 2022-06-29 | 한국재료연구원 | Copper-Tin alloy for hot rolling and method for manufacturing thereof |
Also Published As
Publication number | Publication date |
---|---|
JPS63235455A (en) | 1988-09-30 |
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