JP2849698B2 - Manganese-based vibration-damping alloy and its manufacturing method - Google Patents
Manganese-based vibration-damping alloy and its manufacturing methodInfo
- Publication number
- JP2849698B2 JP2849698B2 JP6052590A JP5259094A JP2849698B2 JP 2849698 B2 JP2849698 B2 JP 2849698B2 JP 6052590 A JP6052590 A JP 6052590A JP 5259094 A JP5259094 A JP 5259094A JP 2849698 B2 JP2849698 B2 JP 2849698B2
- Authority
- JP
- Japan
- Prior art keywords
- manganese
- alloy
- damping alloy
- annealing
- vibration
- 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 - Lifetime
Links
- 229910045601 alloy Inorganic materials 0.000 title claims description 35
- 239000000956 alloy Substances 0.000 title claims description 35
- 239000011572 manganese Substances 0.000 title claims description 21
- 238000013016 damping Methods 0.000 title claims description 20
- 229910052748 manganese Inorganic materials 0.000 title claims description 18
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 title claims description 13
- 238000004519 manufacturing process Methods 0.000 title claims description 8
- 238000000137 annealing Methods 0.000 claims description 18
- 229910052802 copper Inorganic materials 0.000 claims description 10
- 238000001816 cooling Methods 0.000 claims description 9
- 229910052782 aluminium Inorganic materials 0.000 claims description 7
- 239000000203 mixture Substances 0.000 claims description 7
- 238000012545 processing Methods 0.000 claims description 7
- 229910052742 iron Inorganic materials 0.000 claims description 6
- 229910052759 nickel Inorganic materials 0.000 claims description 5
- 238000005266 casting Methods 0.000 claims description 4
- 230000001105 regulatory effect Effects 0.000 claims 1
- 239000000463 material Substances 0.000 description 11
- 239000010949 copper Substances 0.000 description 10
- 239000013078 crystal Substances 0.000 description 7
- 230000000694 effects Effects 0.000 description 7
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 5
- 238000010586 diagram Methods 0.000 description 4
- 238000010438 heat treatment Methods 0.000 description 4
- 230000009466 transformation Effects 0.000 description 4
- 229910017566 Cu-Mn Inorganic materials 0.000 description 3
- 229910017871 Cu—Mn Inorganic materials 0.000 description 3
- 229910000831 Steel Inorganic materials 0.000 description 3
- 239000010959 steel Substances 0.000 description 3
- 238000005482 strain hardening Methods 0.000 description 3
- 238000012360 testing method Methods 0.000 description 3
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 3
- 229910000906 Bronze Inorganic materials 0.000 description 2
- 229910000861 Mg alloy Inorganic materials 0.000 description 2
- 230000032683 aging Effects 0.000 description 2
- 238000005275 alloying Methods 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
- 239000012300 argon atmosphere Substances 0.000 description 2
- 239000010974 bronze Substances 0.000 description 2
- 238000005097 cold rolling Methods 0.000 description 2
- KUNSUQLRTQLHQQ-UHFFFAOYSA-N copper tin Chemical compound [Cu].[Sn] KUNSUQLRTQLHQQ-UHFFFAOYSA-N 0.000 description 2
- 239000011888 foil Substances 0.000 description 2
- 230000033001 locomotion Effects 0.000 description 2
- 230000007246 mechanism Effects 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- HLXZNVUGXRDIFK-UHFFFAOYSA-N nickel titanium Chemical compound [Ti].[Ti].[Ti].[Ti].[Ti].[Ti].[Ti].[Ti].[Ti].[Ti].[Ti].[Ni].[Ni].[Ni].[Ni].[Ni].[Ni].[Ni].[Ni].[Ni].[Ni].[Ni].[Ni].[Ni].[Ni] HLXZNVUGXRDIFK-UHFFFAOYSA-N 0.000 description 2
- 229910001000 nickel titanium Inorganic materials 0.000 description 2
- 238000007711 solidification Methods 0.000 description 2
- 230000008023 solidification Effects 0.000 description 2
- 229910000881 Cu alloy Inorganic materials 0.000 description 1
- 229910000914 Mn alloy Inorganic materials 0.000 description 1
- 238000010521 absorption reaction Methods 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 210000001787 dendrite Anatomy 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 238000006073 displacement reaction Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 239000000835 fiber Substances 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 230000001939 inductive effect Effects 0.000 description 1
- 239000002648 laminated material Substances 0.000 description 1
- 150000002696 manganese Chemical class 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 239000011347 resin Substances 0.000 description 1
- 229920005989 resin Polymers 0.000 description 1
- 102220253765 rs141230910 Human genes 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- 229910052725 zinc Inorganic materials 0.000 description 1
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- Building Environments (AREA)
Description
【産業上の利用分野】この発明は、マンガン基性振合金
とその製造法に関するものである。さらに詳しくは、こ
の発明は、加工性に優れ、製品の形状、大きさの自由度
が高く、しかも鋳造状態として優れた性能を現出させる
ことのできる、騒音、振動対策に有用な、新しいマンガ
ン基性振合金とその製造法に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a manganese-based vibration alloy and a method for producing the same. More specifically, the present invention relates to a new manganese alloy which is excellent in workability, has a high degree of freedom in the shape and size of a product, and can exhibit excellent performance in a cast state, and is useful for noise and vibration countermeasures. The present invention relates to a basic vibration alloy and a method for producing the same.
【従来の技術とその課題】制振材料を歴史的に顧みれ
ば、タイプは一体型か、板を張合わせた積層型とに大別
される。最近は積層型のひとつである制振鋼板が開発さ
れている。制振鋼板は鋼板と樹脂あるいはその他の材料
との複数の板の積層構造であるため、溶接性や成形加工
性あるいは製品の大きさや形状に致命的な制約があり、
従って、主として容器か覆いの用途で大きな成果が報告
されている。これに対し、一体型構造からなる材料はそ
のような制約はなく、これまでに多くの研究がある。Ｍ
ｎ−Ｃｕ合金、Ｃｕ−Ｍｎ合金、アルミブロンズ、マグ
ネシュウム合金、ニチノールなどが知られている。 た
とえば、ＤｅａｎらはＭｎをベースとした合金の研究に
おいて、Ｍｎ基合金は制振材料として可能性が高いこと
を指摘し（Ｅｌｅｃｔｒｏｌｙｔｉｃ Ｍａｇａｎｅｓ
ｅ ａｎｄ １ｔｓ Ａｌｌｏｙｓ， Ｒｏｎａｌｄ
Ｐｒｅｓｓ Ｃｏｍｐ．，Ｎｅｗ Ｙｏｒｋ（１９５
２），１２３）、Ｊａｎｅｓらは、Ｍ ａｎｄ Ｅｎ
ｇ．４（（１９６９），１）。その後、実際にはＣｕを
ベースとしてＣｕ−Ｍｎ系合金が開発されてきている。
しかしながら、これらはいずれも鋳造材であり、加工性
に難があり、性能も対数減衰率で０．３程度が最高値で
あった。そこで、この発明は、従来の一体型材料の欠点
を解消し、一体型材料であり、しかも、従来にない高い
性能を擁し、加工性が高いため、大型鋳物をはじめ、板
・棒・維線・箔などの幅広い形状に対応でき、広範な産
業分野に利用することのできる新しいマンガン（Ｍｎ）
ベースの制振合金の開発に注力してきた。2. Description of the Related Art In the past, damping materials are broadly classified into an integrated type and a laminated type in which plates are laminated. Recently, damping steel sheets, which are one of the laminated types, have been developed. Since the damping steel sheet has a laminated structure of multiple sheets of steel sheet and resin or other materials, there are fatal restrictions on the weldability, formability, and the size and shape of the product,
Therefore, significant results have been reported primarily for container or wrap applications. On the other hand, a material having an integral structure does not have such a restriction, and many studies have been made so far. M
An n-Cu alloy, Cu-Mn alloy, aluminum bronze, magnesium alloy, nitinol and the like are known. For example, in a study of Mn-based alloys, Dean et al. Pointed out that Mn-based alloys are likely to be damping materials (Electrolytic Magneses).
e and 1ts Alloys, Ronald
Press Comp. , New York (195
2), 123), Janes et al., Man and En
g. 4 ((1969), 1). Since then, Cu-Mn based alloys have actually been developed based on Cu.
However, these are all cast materials, and have difficulties in workability, and the performance is the highest at about 0.3 in logarithmic decrement. Therefore, the present invention solves the drawbacks of the conventional integrated material, and is an integrated material, and has unprecedented high performance and high workability.・ New manganese (Mn) that can be used for a wide range of shapes such as foil and can be used in a wide range of industrial fields
Focused on the development of base damping alloys.
【課題を解決するための手段】この発明は、以上の通り
の事情を踏まえてなされたものであって、上記の課題を
解決するものとして、Ｍｎをベースとし、基本組成とし
て、原子％で、Ｃｕ：２０±５％、Ｎｉ：５±３％、Ｆ
ｅ：２±１％を含有するマンガン基制振合金、および、
Ｍｎをベースとし、原子％で、Ｃｕ：２０±５％、Ｎ
ｉ：５±３％、Ｆｅ：２±１％、Ａｌ：２〜５％を含有
するマンガン基制振合金を提供するものである。そして
また、この発明は、上記組成の合金を、その鋳造後およ
び／または加工後に８００〜１１００℃で焼鈍し、徐炉
冷することを特徴とするマンガン基制振合金の製造法を
も提供する。SUMMARY OF THE INVENTION The present invention has been made in view of the above circumstances, and has been made in order to solve the above-mentioned problems. Cu: 20 ± 5%, Ni: 5 ± 3%, F
e: a manganese-based damping alloy containing 2 ± 1%, and
Based on Mn, in atomic%, Cu: 20 ± 5%, N
An object of the present invention is to provide a manganese-based vibration damping alloy containing i: 5 ± 3%, Fe: 2 ± 1%, and Al: 2 to 5%. The present invention also provides a method for producing a manganese-based vibration damping alloy, which comprises annealing the alloy having the above composition at 800 to 1100 ° C. after casting and / or working, and then gradually cooling the alloy. .
【作用】振動を吸収する機構は幾種類かあるが、この発
明の合金系においては、マルテンサイト変態を惹起させ
てその生成相である双晶の運動によって振動を吸収する
機構と考えれる。従来は双晶を得るために銅の含有量を
高める必要がある反面、後に時効によって変態点の上昇
を行なっていた。このような処理によって生じた状態は
不安定であることを回避できない。これに対して、この
発明の制振合金の場合には、変態点を室温近傍に位置す
るようにＣｕ含有量を下げ、代わって、複数元素の合金
化によって振動吸収に適した双晶を形成させる。すなわ
ち、双晶の運動を阻害する分散粒子の生成を極力抑え、
かつ、双晶の生成温度を高めるようにするために合金元
素相互間の共存が可能となるように合金を構成する元素
の種類と添加量を厳密に選定したものである。実際、Ｃ
ｕの含有量を４０〜６０原子％にするとその偏析が大き
く、所要の特性が得られない。このため、この発明で
は、上記の通りの元素を特有の組成割合として採用する
ことが欠かせない。もちろん、上記の基本組成について
は、原料、製造条件等に対応しての若干の変更があるこ
とも常識的に許容されることは言うまでもない。たとえ
ば不可避的不純物の混入も常識的に考慮される。従来の
積層型材料は貼り合わせ工程に高度な技術や膨大な設備
費が欠かせず、一体型材料の場合には、Ｍｎ−Ｃｕ系、
Ｃｕ−Ｍｎ系では銅の含有量が高いほど材料費がかさ
み、かつ、時効処理などの累加作業が不可避となり、コ
ストに加算される。アルミブロンズ、マグネシウム合
金、ニチノールなどは所望の形状に加工すること自体に
多大な経費が必要である。しかし、この発明の合金は、
焼鈍だけで十分な性能が生じ、加工性は形状を問うこと
がないほど容易であり、従来加工コストの面で利用でき
なかった領域に可能性が得られる。焼鈍は８００〜１１
００℃、より好ましくは９００〜１０００℃の温度で行
うこととする。また、所要の特性を得るためには、この
温度から徐冷することが欠かせない。次に、この発明の
実施例を参考例とともに示し、さらに詳しくこの発明の
制振合金とその製造法について説明する。There are several types of mechanisms for absorbing vibration. In the alloy system of the present invention, it is considered to be a mechanism for inducing a martensitic transformation and absorbing the vibration by the movement of a twin, which is a generation phase thereof. Conventionally, the content of copper must be increased to obtain twins, but the transformation point is increased by aging later. The state generated by such processing cannot be prevented from being unstable. On the other hand, in the case of the damping alloy of the present invention, the Cu content is reduced so that the transformation point is located near room temperature, and instead, twins suitable for vibration absorption are formed by alloying a plurality of elements. Let it. In other words, the generation of dispersed particles that inhibit the twinning motion is minimized,
In addition, the types and amounts of elements constituting the alloy are strictly selected so that alloying elements can coexist in order to increase the twinning temperature. In fact, C
When the content of u is 40 to 60 atomic%, the segregation is large, and required characteristics cannot be obtained. Therefore, in the present invention, it is indispensable to employ the above-described elements as a specific composition ratio. Of course, it is needless to say that the basic composition described above may be slightly changed according to the raw materials, production conditions, and the like. For example, mixing of inevitable impurities is also considered with common sense. Conventional laminated materials require advanced technology and enormous equipment costs for the bonding process. In the case of integrated materials, Mn-Cu
In the Cu-Mn system, the higher the copper content, the higher the material cost, and the additional work such as aging treatment is inevitable, which is added to the cost. Processing of aluminum bronze, magnesium alloy, nitinol, and the like into a desired shape requires a great deal of expense. However, the alloy of the present invention
Sufficient performance is produced only by annealing, and the workability is so easy that the shape is not questioned, and the possibility is obtained in a region that could not be used conventionally in terms of processing cost. Annealing 800 ~ 11
It is performed at a temperature of 00 ° C., more preferably 900 to 1000 ° C. In order to obtain required characteristics, it is indispensable to gradually cool from this temperature. Next, examples of the present invention are shown together with reference examples, and the vibration damping alloy of the present invention and a method for producing the same are described in more detail.
【実施例】参考例１〜１２ 成形加工性を高めるために銅の添加量を下げ、また、常
温近傍に変態点を移動させる狙いからマンガンに対し銅
を２０％（原子％）に設定し、それに第３元素として数
種類の元素を添加し制振性能におよぼす第３元素の影響
を評価した。実施例、参考例および比較例として取り上
げる合金は、２種類の方法によって溶製した。つまり、
等軸晶鋳塊と一方向凝固鋳塊である。ともに溶解は高周
波炉を用い、アルゴン雰囲気下で行った。等軸晶鋳塊は
９００℃〜１０００℃に加熱し、熱間圧延で２０ｍｍ角
にまで鍛造し、再び中間焼鈍を行い、５ｍｍまで熱間圧
延した。冷間加工はその熱延板を焼鈍し、水冷後に行っ
た。９０％以上の冷間加工が途中の焼鈍を施すことなく
可能であった。制振性能の測定は冷間加工後に焼鈍し、
所定の冷却速度を施した試片について行った。一方向凝
固鋳塊は、水冷銅盤上に発熱鋳型を設置して上から湯を
注入して作製した。これらの操作は高周波炉チャンバー
内に組み込み、アルゴン雰囲気下で行った。鋳塊のサイ
ズは厚さ２０、高さ９０、幅１７０ｍｍである。鋳型の
上部中央に穴の開いた発熱ボードの蓋をかぶせ、その上
に押湯を兼ねたロートを設置し、注湯した。得られた鋳
塊は下面から上に向かって一方向に柱状晶を呈した組織
であった。柱状晶の成長方向が試料の板面の垂直方向を
一致するような試片をＢ板、柱状晶の成長方向が幅方向
に揃った試片をＣ板、柱状晶の成長方向が試片の長手方
向に平行にある試片をＤ板と称呼して説明する。各試片
は鋳塊から直接ワイヤ−ソ−によって厚さ１ｍｍ〜５ｍ
ｍの板状試片に切削加工して準備した。柱状晶の内部に
は複数のデンドライトが柱状晶の成長方向にほぼ平行に
存在していた。制振機能は、その評価方法の一つである
対数減衰率をもって測定した。試片は厚さが１〜０．５
ｍｍ、幅が１２ｍｍ、長さが７０ｍｍの短冊状試片を用
いた。片持ち梁式で、変位はチャック部の最大歪振幅が
２×１０-4位になるように設置して行った。表１は、Ｍ
ｎ−２０Ｃｕ合金に対して各種の第３元素を添加し性能
改善を試みた結果である。熱処理・鋳造・冷延を経て１
ｍｍ厚にした試片を焼鈍し、その温度から炉冷と空冷に
よって冷却した場合の値を示してある。第３元素を含ま
ないＭｎ−２０Ｃｕの空冷材の対数減衰率０．１６を基
準にすれば、合金添加が有効とみられる元素はＮｉ、Ｆ
ｅ、Ｃｏ、Ｖ、Ａｌ、Ｚｎであることがわかる。なかで
も、参考例２の５Ｎｉが最高を示した。 REFERENCE EXAMPLES 1-12 The amount of copper added was reduced in order to improve the formability, and copper was set to 20% (atomic%) with respect to manganese with the aim of shifting the transformation point to around normal temperature. Then, several kinds of elements were added as the third element, and the influence of the third element on the vibration damping performance was evaluated. The alloys taken as examples, reference examples and comparative examples were produced by two methods. That is,
An equiaxed ingot and a directionally solidified ingot. In both cases, melting was performed in an argon atmosphere using a high-frequency furnace. The equiaxed ingot was heated to 900 ° C. to 1000 ° C., forged to a 20 mm square by hot rolling, subjected to intermediate annealing again, and hot rolled to 5 mm. The cold working was performed after annealing the hot rolled sheet and cooling with water. 90% or more of cold working was possible without intermediate annealing. For the measurement of vibration damping performance, annealing after cold working,
The test was performed on a test piece subjected to a predetermined cooling rate. The unidirectionally solidified ingot was prepared by placing a heat generating mold on a water-cooled copper plate and pouring hot water from above. These operations were incorporated in a high-frequency furnace chamber and performed under an argon atmosphere. The size of the ingot is thickness 20, height 90, and width 170mm. A lid of a heat-generating board with a hole was put on the upper center of the mold, and a funnel serving also as a hot water was placed on top of the lid and poured. The obtained ingot had a structure showing columnar crystals in one direction from the lower surface to the upper side. A specimen in which the growth direction of the columnar crystals coincides with the vertical direction of the plate surface of the sample is a B plate, a specimen in which the growth directions of the columnar crystals are aligned in the width direction is a C plate, and the growth direction of the columnar crystals is a specimen. The specimen parallel to the longitudinal direction will be described as a D-plate. Each specimen is 1mm to 5m thick by wire saw directly from the ingot
m was prepared by cutting a plate-like specimen. A plurality of dendrites existed inside the columnar crystals almost parallel to the growth direction of the columnar crystals. The damping function was measured by a logarithmic decay rate which is one of the evaluation methods. The specimen has a thickness of 1 to 0.5
mm, a width of 12 mm, and a length of 70 mm were used. The displacement was performed by using a cantilever beam so that the maximum strain amplitude of the chuck portion was about 2 × 10 −4 . Table 1 shows M
This is a result of an attempt to improve performance by adding various third elements to an n-20Cu alloy. 1 after heat treatment, casting and cold rolling
The values in the case where the specimen having a thickness of mm was annealed and cooled by furnace cooling and air cooling from that temperature are shown. Based on the logarithmic decrement of 0.16 of the Mn-20Cu air-cooled material that does not contain the third element, the elements for which alloy addition is considered to be effective are Ni, F
e, Co, V, Al, and Zn. Above all, 5Ni of Reference Example 2 showed the highest.
【表１】 実施例１〜３および参考例１３〜１５ 表１の最も有望視できるＭｎ−２０Ｃｕ−５Ｎｉ合金に
対し、上記参考例と同様にして第４元素としてＦｅ、第
５元素としてＡｌを表２に示す割合添加した合金を製造
した。表２は、その結果を示したものである。参考例と
して、第４元素としてＣｒ、Ａｌを表２に示す割合添加
した合金も製造したものも示している。Ｍｎ−２０Ｃｕ
−５Ｎｉに対し、２Ｆｅを添加した実施例１が最高であ
り、ついで実施例３の２Ｆｅ−５Ａｌならびに実施例２
の２Ｆｅ−５Ａｌ合金と続いている。[Table 1] Examples 1 to 3 and Reference Examples 13 to 15 For the most promising Mn-20Cu-5Ni alloys in Table 1, Fe and Al as the fourth element are shown in Table 2 in the same manner as in the above Reference Example. Proportionally added alloys were produced. Table 2 shows the results. As a reference example, an alloy in which Cr and Al are added as the fourth element in the proportions shown in Table 2 is also shown. Mn-20Cu
Example 1 in which 2Fe was added to -5Ni was the best, then 2Fe-5Al of Example 3 and Example 2
2Fe-5Al alloy.
【表２】 図１〜図４は、上記に基づいて得られた最高値を示すＭ
ｎ−２０Ｃｕ−５Ｎｉ−２Ｆｅ（以降、Ｍ２０５２合金
と呼ぶ）の一方向凝固鋳塊を用いた各種板の対数減衰率
におよぼす熱処理並びに加工の影響を示したものであ
る。図１は、鋳造のままのＢ板の対数減衰率におよぼす
９００ならびに１０００℃から炉冷した場合の焼鈍時間
の影響である。バラツキは大きいが、９００℃４８時間
処理では０．７２が得られた。表１では０．２８が、表
２では０．３２がそれぞれ最高であったが、本図にはそ
れらを遥かに超えた値である。図２は、鋳造のままのＣ
板の対数減衰率におよぼす９００ならびに１０００℃か
ら炉冷した場合の焼鈍時間の影響である。前図の値に比
べ全体が低い値を呈し、０．３を超えてはいない。 図
３は、鋳造のままのＤ板の対数減衰率におよぼす９００
ならびに１０００℃から炉冷した場合の焼鈍時間の影響
である。図１、図２のいずれより全体的に高いといえ
る。９００℃５時間と１０００℃５時間では０．７が生
じている。図４は、Ｂ・Ｃ・Ｄ板のそれぞれを９０％冷
延した後の対数減衰率におよぼす焼鈍時間の影響を示
す。Ｂ・Ｄ板は冷延によって性能は劣化するのに対し、
Ｃ板は逆に向上し、９００℃２４時間では０．７の値も
みられる。Ｍ２０５２合金は等軸晶鋳塊の場合、加工と
熱処理によって最低でも対数減衰率は０．３は保証でき
る。一方向凝固の試験からわかるように、凝固状態ある
いは柱状晶の成長方向に対する加工と熱処理の組み合せ
によっては０．７を超す値を得ることができる。[Table 2] 1 to 4 show the maximum values M obtained based on the above.
It shows the influence of heat treatment and processing on the logarithmic decrement of various plates using a unidirectionally solidified ingot of n-20Cu-5Ni-2Fe (hereinafter referred to as M2052 alloy). FIG. 1 shows the effect of the annealing time when the furnace is cooled from 900 and 1000 ° C. on the logarithmic decrement of the as-cast B plate. Although the variation was large, 0.72 was obtained by the treatment at 900 ° C. for 48 hours. In Table 1, 0.28 was the highest, and in Table 2, 0.32 was the highest, respectively, but in this figure, the values far exceeded them. FIG. 2 shows the as-cast C
This is the effect of the annealing time when the furnace is cooled from 900 and 1000 ° C. on the logarithmic decrement of the sheet. The overall value is lower than the value in the previous figure, and does not exceed 0.3. FIG. 3 shows the effect of 900 on the logarithmic decrement of the as-cast D-plate.
And the effect of the annealing time when the furnace is cooled from 1000 ° C. It can be said that it is generally higher than either of FIGS. At 900 ° C. for 5 hours and at 1000 ° C. for 5 hours, 0.7 occurs. FIG. 4 shows the effect of annealing time on the logarithmic decrement after each of the B, C, and D plates was cold rolled by 90%. The performance of B and D plates deteriorates due to cold rolling,
On the contrary, the C-plate improved, and a value of 0.7 was observed at 900 ° C. for 24 hours. When the M2052 alloy is an equiaxed ingot, at least a logarithmic decrement of 0.3 can be guaranteed by processing and heat treatment. As can be seen from the unidirectional solidification test, a value exceeding 0.7 can be obtained depending on the combination of processing and heat treatment in the solidification state or the growth direction of columnar crystals.
【発明の効果】この発明により、以上詳しく説明した通
り、高い性能の非積層型のマンガン基制振合金であり、
加工性が優れ、製品の形状・大きさの自由度が高く、し
かも鋳造状態として優れた性能が得られることから、板
・棒・線材・箔・繊維などの幅広い形状に対応でき、騒
音や振動対策の必要な広範な産業分野に寄与し得る。According to the present invention, as described in detail above, a high-performance non-laminated manganese-based vibration damping alloy is provided.
Excellent workability, high degree of freedom in the shape and size of the product, and excellent performance in the cast state, so it can handle a wide range of shapes such as plates, rods, wires, foils, and fibers, and has noise and vibration. It can contribute to a wide range of industrial fields that require measures.
【図１】Ｂ板の対数減衰率におよぼす９００℃ならびに
１０００℃から炉冷した場合の焼鈍時間の影響を示した
図である。FIG. 1 is a diagram showing the effect of annealing time when furnace cooling is performed from 900 ° C. and 1000 ° C. on the logarithmic decrement of a B plate.
【図２】Ｃ板の対数減衰率におよぼす９００℃ならびに
１０００℃から炉冷した場合の焼鈍時間の影響を示した
図である。FIG. 2 is a diagram showing the influence of the annealing time when the furnace is cooled from 900 ° C. and 1000 ° C. on the logarithmic decrement of the C plate.
【図３】Ｄ板の対数減衰率におよぼす９００℃ならびに
１０００℃から炉冷した場合の焼鈍時間の影響を示した
図である。FIG. 3 is a diagram showing the influence of the annealing time upon furnace cooling from 900 ° C. and 1000 ° C. on the logarithmic decrement of the D plate.
【図４】Ｂ・Ｃ・Ｄ板のそれぞれの９０％冷延材の対数
減衰率におよぼす９００℃ならびに１０００℃から炉冷
した場合の焼鈍時間の影響を示した図である。FIG. 4 is a diagram showing the effect of annealing time when furnace cooling is performed from 900 ° C. and 1000 ° C. on the logarithmic decrement of 90% cold-rolled material of each of the B, C, and D plates.
───────────────────────────────────────────────────── フロントページの続き (56)参考文献 特開 昭48−71310（ＪＰ，Ａ) 特開 昭51−133120（ＪＰ，Ａ) 特開 昭49−23116（ＪＰ，Ａ) 特開 昭50−136212（ＪＰ，Ａ) 特開 昭51−29310（ＪＰ，Ａ) 特開 昭50−127817（ＪＰ，Ａ) (58)調査した分野(Int.Cl.6，ＤＢ名) C22C 22/00 C22F 1/16──────────────────────────────────────────────────続 き Continuation of the front page (56) References JP-A-48-71310 (JP, A) JP-A-51-133120 (JP, A) JP-A-49-23116 (JP, A) JP-A 50-113 136212 (JP, A) JP-A-51-29310 (JP, A) JP-A-50-127817 (JP, A) (58) Fields investigated (Int. Cl. 6 , DB name) C22C 22/00 C22F 1 / 16
Claims (4)
子％で、Ｃｕ：２０±５％、Ｎｉ：５±３％、Ｆｅ：２
±１％を含有するマンガン規制振合金。1. Based on Mn, as a basic composition, in atomic%, Cu: 20 ± 5%, Ni: 5 ± 3%, Fe: 2
Manganese regulated alloy containing ± 1%.
子％で、Ｃｕ：２０±５％、Ｎｉ：５±３％、Ｆｅ：２
±１％とともにＡｌ：２〜５％を含有するマンガン基制
振合金。2. Based on Mn, as a basic composition, in atomic%, Cu: 20 ± 5%, Ni: 5 ± 3%, Fe: 2
Manganese-based vibration damping alloy containing Al: 2 to 5% together with ± 1%.
子％で、Ｃｕ：２０±５％、Ｎｉ：５±３％、Ｆｅ：２
±１％を含有するマンガン基制振合金の鋳造後および／
または加工後に８００〜１１００℃で焼鈍し、徐炉冷す
ることを特徴とするマンガン基制振合金の製造法。3. Based on Mn, as a basic composition, in atomic%, Cu: 20 ± 5%, Ni: 5 ± 3%, Fe: 2
After casting of manganese-based damping alloy containing ± 1% and / or
Alternatively, a method for producing a manganese-based vibration-damping alloy, comprising annealing at 800 to 1100 ° C. after working and cooling slowly.
子％で、Ｃｕ：２０±５％、Ｎｉ：５±３％、Ｆｅ：２
±１％、Ａｌ：２〜５％を含有するマンガン基制振合金
の鋳造後および／または加工後に８００〜１１００℃で
焼鈍し、徐炉冷することを特徴とするマンガン基制振合
金の製造法。4. Based on Mn, as a basic composition, in atomic%, Cu: 20 ± 5%, Ni: 5 ± 3%, Fe: 2
Manufacture of a manganese-based damping alloy characterized by annealing at 800 to 1100 ° C after casting and / or processing of a manganese-based damping alloy containing ± 1% and Al: 2 to 5%, followed by annealing at a slow rate. Law.
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|---|---|---|---|
| JP6052590A JP2849698B2 (en) | 1994-02-28 | 1994-02-28 | Manganese-based vibration-damping alloy and its manufacturing method |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6052590A JP2849698B2 (en) | 1994-02-28 | 1994-02-28 | Manganese-based vibration-damping alloy and its manufacturing method |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH07242977A JPH07242977A (en) | 1995-09-19 |
| JP2849698B2 true JP2849698B2 (en) | 1999-01-20 |
Family
ID=12919012
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP6052590A Expired - Lifetime JP2849698B2 (en) | 1994-02-28 | 1994-02-28 | Manganese-based vibration-damping alloy and its manufacturing method |
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2005028910A1 (en) * | 2003-09-24 | 2005-03-31 | Bridgestone Corporation | Vibration absorbing alloy member, and rubber vibration isolator, floor vibration damping apparatus, tire, steel cord and rubber sesmic isolatior using the same |
| JP2008005896A (en) * | 2006-06-27 | 2008-01-17 | Nobuaki Hayashi | Scissors |
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|---|---|---|---|---|
| JP2005200722A (en) * | 2004-01-16 | 2005-07-28 | Daido Steel Co Ltd | Method for imparting corrosion resistance to manganese-based twin-type damping alloys |
| JP2006300715A (en) * | 2005-04-20 | 2006-11-02 | Ono Sokki Co Ltd | Torque sensor |
| JP4687983B2 (en) * | 2006-05-10 | 2011-05-25 | 大同特殊鋼株式会社 | Method for producing Mn-Cu vibration damping alloy |
| JP4744420B2 (en) * | 2006-11-10 | 2011-08-10 | 独立行政法人物質・材料研究機構 | Manufacturing method of high temperature damping manganese-based alloy |
| JP5076609B2 (en) * | 2007-04-17 | 2012-11-21 | 大同特殊鋼株式会社 | Mn-Cu vibration damping alloy and manufacturing method thereof |
| JP5136083B2 (en) * | 2008-01-25 | 2013-02-06 | 大同特殊鋼株式会社 | Mn-based twinned damping alloy and damping parts or damping products |
| WO2010041532A1 (en) | 2008-10-10 | 2010-04-15 | 株式会社豊田自動織機 | Iron alloy, iron alloy member and manufacturing method therefor |
| CN103966493B (en) * | 2014-05-09 | 2015-08-26 | 曹帅 | A kind of high damping Mn-Cu base noiseless alloy and preparation method thereof |
| CN103981396B (en) * | 2014-05-09 | 2016-03-23 | 曹帅 | A kind of high damping Mn-Ni base noiseless alloy and preparation method thereof |
| CN107012417B (en) * | 2017-06-06 | 2018-06-19 | 东北大学 | A kind of preparation method of high-intensity high-damping MnCu based alloys |
| CN113430434B (en) * | 2021-05-20 | 2022-08-09 | 上海大学 | High-damping manganese-copper alloy for wide-temperature-zone service and preparation method thereof |
Family Cites Families (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS4871310A (en) * | 1971-12-28 | 1973-09-27 | ||
| JPS4923116A (en) * | 1972-06-24 | 1974-03-01 | ||
| JPS5334099B2 (en) * | 1974-03-28 | 1978-09-19 | ||
| JPS50136212A (en) * | 1974-04-19 | 1975-10-29 | ||
| JPS5129310A (en) * | 1974-09-05 | 1976-03-12 | Mitsubishi Heavy Ind Ltd | Shaonkokaojusuru boshingokin |
| JPS51133120A (en) * | 1975-05-16 | 1976-11-18 | Komatsu Ltd | Mn-cu silent alloy |
-
1994
- 1994-02-28 JP JP6052590A patent/JP2849698B2/en not_active Expired - Lifetime
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2005028910A1 (en) * | 2003-09-24 | 2005-03-31 | Bridgestone Corporation | Vibration absorbing alloy member, and rubber vibration isolator, floor vibration damping apparatus, tire, steel cord and rubber sesmic isolatior using the same |
| JP2008005896A (en) * | 2006-06-27 | 2008-01-17 | Nobuaki Hayashi | Scissors |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH07242977A (en) | 1995-09-19 |
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