JP6142411B2 - Method for producing Fe-Al alloy - Google Patents
Method for producing Fe-Al alloy Download PDFInfo
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- JP6142411B2 JP6142411B2 JP2012267966A JP2012267966A JP6142411B2 JP 6142411 B2 JP6142411 B2 JP 6142411B2 JP 2012267966 A JP2012267966 A JP 2012267966A JP 2012267966 A JP2012267966 A JP 2012267966A JP 6142411 B2 JP6142411 B2 JP 6142411B2
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- 229910000838 Al alloy Inorganic materials 0.000 title claims description 98
- 238000004519 manufacturing process Methods 0.000 title claims description 36
- 238000000034 method Methods 0.000 claims description 50
- 230000008569 process Effects 0.000 claims description 44
- 238000001816 cooling Methods 0.000 claims description 41
- 229910045601 alloy Inorganic materials 0.000 claims description 37
- 239000000956 alloy Substances 0.000 claims description 37
- 238000000137 annealing Methods 0.000 claims description 34
- 238000005097 cold rolling Methods 0.000 claims description 17
- 229910052782 aluminium Inorganic materials 0.000 claims description 7
- 239000012535 impurity Substances 0.000 claims description 5
- 238000013016 damping Methods 0.000 description 28
- 239000013078 crystal Substances 0.000 description 23
- 239000000463 material Substances 0.000 description 14
- 230000004048 modification Effects 0.000 description 10
- 238000012986 modification Methods 0.000 description 10
- 239000002245 particle Substances 0.000 description 10
- 238000002441 X-ray diffraction Methods 0.000 description 7
- 230000009467 reduction Effects 0.000 description 7
- 229910015372 FeAl Inorganic materials 0.000 description 5
- 238000004458 analytical method Methods 0.000 description 5
- 239000000203 mixture Substances 0.000 description 5
- 230000035699 permeability Effects 0.000 description 5
- 229910000859 α-Fe Inorganic materials 0.000 description 5
- 238000009413 insulation Methods 0.000 description 4
- 229910052742 iron Inorganic materials 0.000 description 4
- 238000005096 rolling process Methods 0.000 description 4
- 230000015572 biosynthetic process Effects 0.000 description 3
- 230000003247 decreasing effect Effects 0.000 description 3
- 238000002003 electron diffraction Methods 0.000 description 3
- 238000010438 heat treatment Methods 0.000 description 3
- 229910000765 intermetallic Inorganic materials 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 229910000881 Cu alloy Inorganic materials 0.000 description 2
- 150000001875 compounds Chemical class 0.000 description 2
- 238000010411 cooking Methods 0.000 description 2
- 239000011162 core material Substances 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 229910052760 oxygen Inorganic materials 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 238000007711 solidification Methods 0.000 description 2
- 230000008023 solidification Effects 0.000 description 2
- 229910002060 Fe-Cr-Al alloy Inorganic materials 0.000 description 1
- 229910000861 Mg alloy Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 230000001747 exhibiting effect Effects 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 238000009774 resonance method Methods 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 238000012916 structural analysis Methods 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 238000010998 test method Methods 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 238000004227 thermal cracking Methods 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
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Description
本発明はＡｌ濃度の“ゆらぎ“、すなわち合金中に金属間化合物が生成される過程において生じる濃度の不均一な状態を有する新規なＦｅ−Ａｌ合金の製造方法に関し、特にＡｌ含有量が６〜１２重量％のものの製造方法に関する。 The present invention relates to a method for producing a novel Fe—Al alloy having a “fluctuation” of the Al concentration, that is, a concentration non-uniform state generated in the process of forming an intermetallic compound in the alloy. The present invention relates to a production method of 12% by weight.
従来、制振性や加工性を備えた金属として、Ｆｅ−Ｃｒ−Ａｌ合金、Ｍｎ−Ｃｕ合金、Ｃｕ合金、Ｍｇ合金等が知られており、様々な用途に使用されている。これらの合金のなかでも、Ａｌ含有量が６〜１０重量％であり、かつ平均結晶粒径が３００〜７００μｍであるＦｅ−Ａｌ合金は、優れた制振性を有しており、制振合金として有用であることが分かっている（例えば、特許文献１参照）。当該Ｆｅ−Ａｌ合金は、塑性加工及び焼鈍処理を行った後に、所定の冷却速度で冷却することにより製造されている。 Conventionally, Fe—Cr—Al alloys, Mn—Cu alloys, Cu alloys, Mg alloys, and the like are known as metals having vibration damping properties and workability, and are used in various applications. Among these alloys, the Fe—Al alloy having an Al content of 6 to 10% by weight and an average crystal grain size of 300 to 700 μm has excellent vibration damping properties. (See, for example, Patent Document 1). The Fe—Al alloy is manufactured by cooling at a predetermined cooling rate after performing plastic working and annealing.
しかしながら、Ａｌ含有量が１２重量％程度以下であるＦｅ−Ａｌ合金の製造方法については、上記以外の方法は殆ど知られていない。また、Ａｌ含有量が１２重量％程度以下であるＦｅ−Ａｌ合金において、その有用な特性を一層向上させ、より実用的価値が高いものにするために、いかなる技術的手段を採用すれば良いかについても一切知られていない。 However, there are few known methods other than those described above for a method for producing an Fe—Al alloy having an Al content of about 12% by weight or less. In addition, what kind of technical means should be adopted in order to further improve the useful characteristics of the Fe-Al alloy having an Al content of about 12% by weight or less and to have higher practical value? There is no known at all.
そこで、本発明は、Ａｌ含有量が６〜１２重量％であるＦｅ−Ａｌ合金であって、優れた制振性を示す、Ａｌ濃度のゆらぎを有するＦｅ−Ａｌ合金の製造方法の提供を目的とした。 Accordingly, the present invention provides a Fe-Al alloy Al content of 6 to 12 wt%, better showing the vibration damping property, the provision of a method of manufacturing a Fe-Al alloys having the fluctuation of the Al concentration It was aimed.
ここで、本発明者が鋭意検討したところ、Ａｌ含有量が１４重量％以上のＦｅ−Ａｌ合金は、脆くて強度面において実用性に欠けるとの問題があることが判明した。また、Ｆｅ−Ａｌ合金については、Ａｌ濃度のゆらぎを有する構造、すなわちＡｌ濃度が不均一な構造とすることにより制振性を向上効果が高まるとの知見に至った。 Here, as a result of intensive studies by the present inventors, it has been found that an Fe-Al alloy having an Al content of 14% by weight or more is brittle and lacks practicality in terms of strength. Further, the present inventors have found that the Fe-Al alloy has a structure having an Al concentration fluctuation, that is, a structure in which the Al concentration is not uniform, thereby improving the vibration damping effect.
ここで、“ゆらぎ“とは、合金中に化合物が生成される過程において生成される濃度の不均一な状態のことである。Ｆｅ−Ａｌ合金では、熱処理でＦｅ３Ａｌが生成されるが、前段階でＡｌ濃度の不均一な状態ができる、この変態過程で生ずるＡｌの濃度の不均一な状態を“ゆらぎ“という。 Here, “fluctuation” means a non-uniform state of concentration generated in the process of forming a compound in the alloy. In the Fe—Al alloy, Fe 3 Al is generated by heat treatment, but the Al concentration is nonuniform in the previous stage. The nonuniform Al concentration generated in this transformation process is called “fluctuation”.
かかる知見に基づき提供される本発明は、Ａｌ含有量６〜１２重量％、残部Ｆｅ及び不可避的不純物からなり、Ａｌ濃度のゆらぎを有することを特徴とするＦｅ−Ａｌ合金である。 The present invention provided on the basis of such findings is an Fe—Al alloy comprising Al content of 6 to 12% by weight, the balance Fe and unavoidable impurities, and having fluctuations in Al concentration.
本発明のＦｅ−Ａｌ合金は、熱処理により、合金中にＦｅ３Ａｌ相が生成される前段階の、Ａｌ濃度のゆらぎを有する。すなわち、本発明のＦｅ−Ａｌ合金は、Ａｌ濃度が部位によって不均一とされていることから、外部から入力された振動エネルギーを吸収し、減衰させることができる。また、本発明のＦｅ−Ａｌ合金は、Ａｌ含有量が６〜１２重量％の範囲内であり、このことにより強度面においても優れた特性を示す。すなわち、Ａｌが１２％以上になると、凝固過程で熱歪が発生して割れが起こる。また結晶粒界に金属間化合物が生成して８００℃以上での熱間加工性が悪くなり、脆くなる。Ａｌが６％以下では、脆性は改善できるものの、Ａｌ濃度の不均一なゆらぎが生成できない。かかる知見に基づき、本発明においては、Ａｌ含有量を６〜１２重量％の範囲内としている。従って、本発明によれば、制振性及び強度面の双方において優れた特性を示すＦｅ−Ａｌ合金を提供できる。 The Fe—Al alloy of the present invention has fluctuations in the Al concentration before the Fe 3 Al phase is generated in the alloy by heat treatment. That is, the Fe—Al alloy of the present invention can absorb and attenuate vibration energy input from the outside because the Al concentration is nonuniform depending on the part. In addition, the Fe-Al alloy of the present invention has an Al content in the range of 6 to 12% by weight, and thus exhibits excellent characteristics in terms of strength. That is, when Al becomes 12% or more, thermal strain is generated in the solidification process and cracks occur. In addition, an intermetallic compound is generated at the crystal grain boundary, resulting in poor hot workability at 800 ° C. or higher and brittleness. When Al is 6% or less, brittleness can be improved, but fluctuations in non-uniform Al concentration cannot be generated. Based on this knowledge, in the present invention, the Al content is in the range of 6 to 12% by weight. Therefore, according to the present invention, it is possible to provide an Fe—Al alloy that exhibits excellent characteristics in both vibration damping properties and strength.
また、本発明のＡｌ濃度のゆらぎを有するＦｅ−Ａｌ合金の製造方法は、下記工程を含むものである。
（１） Ａｌ含有量６〜１２重量％、残部Ｆｅ及び不可避的不純物からなる合金を熱間加工により塑性加工する塑性加工工程。
（２） 塑性加工した合金を冷間圧延加工する冷間圧延工程。
（３） 冷間圧延加工後の合金を磁気変態点を超え、１０００℃以下の温度で焼鈍する焼鈍処理工程。
（４） 焼鈍処理工程の後、常温まで空冷する空冷工程。
Moreover, the manufacturing method of the Fe-Al alloy which has the fluctuation | variation of Al concentration of this invention includes the following process.
(1) A plastic working step of plastic working an alloy comprising Al content of 6 to 12% by weight, the balance Fe and inevitable impurities by hot working.
(2) A cold rolling process in which a plastically worked alloy is cold rolled.
(3) the alloy after cold rolling exceeds the magnetic varying state point, annealing step of annealing at 1000 ° C. or lower.
( 4 ) An air cooling step of air cooling to room temperature after the annealing treatment step.
本発明のＡｌ濃度のゆらぎを有するＦｅ−Ａｌ合金の製造方法のように、工程（３）においてＦｅ−Ａｌ合金に焼鈍処理を施した後、工程（４）において空冷することとした場合についても、工程（３）までの工程を経ることによりＦｅ−Ａｌ合金に加えられていた歪みが解消される。また、Ｆｅ−Ａｌ合金をなす原子が動きやすくなった状態になる。本発明の製造方法においては、このような状態において工程（４）においてＦｅ−Ａｌ合金を常温まで空冷することとしている。これにより、不完全な規則相が混在した結晶構造となり、Ａｌ濃度のゆらぎを有するＦｅ−Ａｌ合金が形成される。このように工程（４）による処理を施す本発明のＦｅ−Ａｌ合金の製造方法は、制振性及び強度を有するＦｅ−Ａｌ合金を製造することが可能となる。 As in the method for producing an Fe—Al alloy having fluctuations in the Al concentration of the present invention, after annealing the Fe—Al alloy in the step ( 3 ), air cooling in the step ( 4 ) is also performed. The strain applied to the Fe—Al alloy is eliminated through the steps up to step (3). Further, the atoms forming the Fe—Al alloy are easily moved. In the production method of the present invention, in such a state, the Fe—Al alloy is air-cooled to room temperature in the step ( 4 ). Thereby, a crystal structure in which incomplete ordered phases are mixed is formed, and an Fe—Al alloy having Al concentration fluctuation is formed. The method of manufacturing a Fe-Al alloy of the present invention which processes according to step (4) as is, it is possible to produce a Fe-Al alloy having a damping property and strength.
本発明によれば、Ａｌ含有量が６〜１２重量％であるＦｅ−Ａｌ合金であって、優れた制振性を示すＦｅ３Ａｌ相が生成される前段階の、Ａｌ濃度のゆらぎを有するＦｅ−Ａｌ合金、及び当該Ｆｅ−Ａｌ合金の製造方法を提供することができる。 According to the present invention, the Fe content is 6 to 12% by weight, and has an Al concentration fluctuation before the formation of the Fe 3 Al phase exhibiting excellent vibration damping properties. An Fe—Al alloy and a method for producing the Fe—Al alloy can be provided.
≪本発明のＦｅ−Ａｌ合金の組成・構造について≫
以下、本発明の一実施形態に係るＦｅ−Ａｌ合金について詳細に説明する。本実施形態のＦｅ−Ａｌ合金は、Ａｌ含有量６〜１２重量％、残部Ｆｅ及び不可避的不純物（ＳｉＯ０．１重量％以下；Ｍｎ０．１重量％以下、；その他Ｃ、Ｎ、Ｓ、Ｏなど併せて０．１重量％以下）からなるものである。Ａｌ含有量は、６〜１２重量％の範囲内であればよいが、好ましくは７〜１０重量％であり、さらに好ましくは７．５〜８．５重量％である。
<< Composition and structure of Fe-Al alloy of the present invention >>
Hereinafter, an Fe—Al alloy according to an embodiment of the present invention will be described in detail. The Fe-Al alloy of this embodiment has an Al content of 6 to 12% by weight, the balance Fe and unavoidable impurities (SiO 0.1% by weight or less; Mn 0.1% by weight or less; other C, N, S, O, etc. And 0.1% by weight or less). Although Al content should just be in the range of 6-12 weight%, Preferably it is 7-10 weight%, More preferably, it is 7.5-8.5 weight%.
本実施形態のＦｅ−Ａｌ合金は、Ａｌ含有量が６〜１２重量％の範囲内でありつつ、Ｆｅ３Ａｌ相が生成される前段階の、Ａｌ濃度のゆらぎを有する点において特徴的である。すなわち、本実施形態のＦｅ−Ａｌ合金は、原子が局所的に規則配列された部位が散在した構造とされており、これに起因してＡｌ濃度のゆらぎ（Ａｌ濃度の不均衡）が生じている。このような構造を有することにより、本実施形態のＦｅ−Ａｌ合金は、外部から入力された振動エネルギーをＡｌ濃度のゆらぎが形成された部位において吸収し、減衰させることができる。従って、本実施形態のＦｅ−Ａｌ合金は、制振性の面において優れた特性を示す。 The Fe—Al alloy of the present embodiment is characteristic in that the Al content is within a range of 6 to 12% by weight, and has an Al concentration fluctuation before the Fe 3 Al phase is generated. . That is, the Fe—Al alloy of the present embodiment has a structure in which the sites in which atoms are regularly arranged locally are scattered, resulting in Al concentration fluctuations (Al concentration imbalance). Yes. By having such a structure, the Fe—Al alloy of the present embodiment can absorb and attenuate vibration energy input from the outside at a site where the fluctuation of the Al concentration is formed. Therefore, the Fe—Al alloy of the present embodiment exhibits excellent characteristics in terms of vibration damping properties.
また、本実施形態のＦｅ−Ａｌ合金は、Ａｌ含有量が６〜１２重量％の範囲内であり、制振性の高さに加えて、強度面においても優れた特性を示す。すなわち、Ａｌ含有量が１２％以上になると、凝固過程で熱割れが発生する。また結晶粒界に金属間化合物が生成して８００℃以上での熱間加工性が低下して脆くなる。一方、Ａｌ含有量が６％以下である場合には、前述したような脆性は改善できるものの、ゆらぎが生成しない。そのため、Ａｌ含有量を６％以下まで低減させると、外部から入力された振動エネルギーをＡｌ濃度のゆらぎが形成された部位において吸収して減衰させる機能（制振機能）が損なわれてしまう。本実施形態のＦｅ−Ａｌ合金は、Ａｌ含有量が６〜１２重量％の範囲内であるため、高強度であり、かつ制振性の面においても優れている。 In addition, the Fe-Al alloy of the present embodiment has an Al content in the range of 6 to 12% by weight, and exhibits excellent characteristics in terms of strength in addition to high vibration damping properties. That is, when the Al content is 12% or more, thermal cracking occurs during the solidification process. In addition, an intermetallic compound is generated at the crystal grain boundary, and the hot workability at 800 ° C. or higher is lowered and becomes brittle. On the other hand, when the Al content is 6% or less, the brittleness as described above can be improved, but fluctuation does not occur. Therefore, if the Al content is reduced to 6% or less, the function (damping function) that absorbs and attenuates vibration energy input from the outside at the site where the fluctuation of the Al concentration is formed is impaired. The Fe—Al alloy of this embodiment has an Al content in the range of 6 to 12% by weight, and thus has high strength and excellent vibration damping properties.
≪本発明のＦｅ−Ａｌ合金の製造方法について≫
続いて、本実施形態のＦｅ−Ａｌ合金の製造方法について説明する。本実施形態のＦｅ−Ａｌ合金の製造方法は、下記の工程（１）〜（５）を経て実施される。
<< About the manufacturing method of the Fe-Al alloy of this invention >>
Then, the manufacturing method of the Fe-Al alloy of this embodiment is demonstrated. The manufacturing method of the Fe-Al alloy of this embodiment is implemented through the following process (1)-(5).
［工程（１）：塑性加工工程］
先ず、Ａｌ含有量６〜１２重量％、残部Ｆｅ及び不可避的不純物からなる合金を塑性加工する。具体的には、まず、Ｆｅ−Ａｌ合金中のＡｌ含有量が所定値となる割合に予め調整したＡｌとＦｅ素材とを、窒素及び酸素の侵入を防止するために、０．１〜０．０１Ｐａ程度の減圧下で溶融した後、鋳型に流し込んで、Ｆｅ−Ａｌ合金鋳塊を得る。その後、得られた合金鋳塊を圧延、鍛造などの塑性加工（熱間加工）と機械加工により、所定の形状に仕上げる。
[Step (1): Plastic working step]
First, an alloy having an Al content of 6 to 12% by weight, the balance Fe and unavoidable impurities is plastically processed. Specifically, first, in order to prevent intrusion of nitrogen and oxygen, Al and Fe material, which have been adjusted in advance to a ratio in which the Al content in the Fe—Al alloy becomes a predetermined value, is 0.1 to 0.00. After melting under a reduced pressure of about 01 Pa, it is poured into a mold to obtain an Fe—Al alloy ingot. Thereafter, the obtained alloy ingot is finished into a predetermined shape by plastic working (hot working) such as rolling and forging and machining.
工程（１）においては、必要に応じて塑性加工後の合金を焼鈍処理に供してもよい。塑性加工後に焼鈍処理することにより、加工性、制振性、高強度等の合金性能を高めることができる。塑性加工後に焼鈍処理を行う場合、その焼鈍条件については特に制限されないが、具体的には、得られた塑性加工後の合金を７００〜１０００℃程度の温度に３０分〜２時間程度保持する条件が例示される。焼鈍処理時の温度及び時間は、合金の組成、塑性加工条件等を考慮して、上記の範囲から適宜選択すればよい。 In the step (1), the alloy after plastic working may be subjected to an annealing treatment as necessary. By performing annealing after plastic working, it is possible to improve alloy performance such as workability, vibration damping and high strength. When annealing is performed after plastic working, the annealing conditions are not particularly limited, but specifically, the conditions for maintaining the obtained plastic worked alloy at a temperature of about 700 to 1000 ° C. for about 30 minutes to 2 hours. Is exemplified. The temperature and time during the annealing treatment may be appropriately selected from the above ranges in consideration of the alloy composition, plastic working conditions, and the like.
［工程（２）：冷間圧延工程］
続いて、上記工程（１）において塑性加工した合金に対して冷間圧延加工を行う。なお、塑性加工後に焼鈍処理を行っている場合には、当該冷間圧延加工は、合金を下記冷間圧延温度にまで冷却した後に実施される。
[Step (2): Cold rolling step]
Subsequently, cold rolling is performed on the alloy plastically processed in the step (1). In addition, when the annealing process is performed after plastic working, the said cold rolling process is implemented after cooling an alloy to the following cold rolling temperature.
工程（２）の冷間圧延加工時の温度条件としては、合金の再結晶温度以下であれば特に制限されないが、通常、常温で行うことができる。また、冷間圧延加工における圧延加工条件は、特に制限されないが、断面減少率が通常５％以上、好ましくは２０％以上、さらに好ましくは２０〜９５％となるような加工条件であることが望ましい。なお、本工程では、１回の冷間圧延加工により上記断面減少率に加工してもよく、また２回以上の冷間圧延加工を行うことにより上記断面減少率に加工してもよい。なお、ここで、「断面減少率」とは、圧延加工前の合金の断面積に対して圧延加工後に減少した断面積の割合（％）であり、下記の（数式１）により算出することができる。 Although it will not restrict | limit especially as temperature conditions at the time of the cold rolling process of a process (2) if it is below the recrystallization temperature of an alloy, Usually, it can carry out at normal temperature. Further, the rolling process conditions in the cold rolling process are not particularly limited, but it is desirable that the cross-section reduction rate is usually 5% or more, preferably 20% or more, more preferably 20 to 95%. . In addition, in this process, you may process into the said cross-sectional reduction rate by one cold rolling process, and you may process into the said cross-sectional reduction rate by performing the cold rolling process twice or more. Here, the “cross-sectional reduction rate” is the ratio (%) of the cross-sectional area decreased after rolling with respect to the cross-sectional area of the alloy before rolling, and can be calculated by the following (Equation 1). it can.
断面減少率［％］＝｛１−（加工後の合金の断面積）／（加工前の合金の断面積）｝×１００ ・・・ （数式１） Cross-sectional reduction rate [%] = {1- (Cross sectional area of alloy after processing) / (Cross sectional area of alloy before processing)} × 100 (Equation 1)
［工程（３）：焼鈍処理工程］
次いで、冷間圧延加工した合金に対して焼鈍処理を行う。具体的には、冷間圧延加工を施した合金を磁気変態点（６８７℃）以上であって、１０００℃（好ましくは８５０℃）以下の温度に３０分〜２時間程度保持して、焼鈍処理する。焼鈍処理時の温度及び時間は、合金の組成、塑性加工条件等を考慮して、上記の範囲から適宜選択すればよい。
[Step (3): Annealing treatment step]
Next, an annealing treatment is performed on the cold-rolled alloy. Specifically, there is an alloy subjected to cold rolling magnetic varying state point (687 ° C.) or higher, 1000 ° C. (preferably 850 ° C.) to a temperature below the holding about 30 minutes to 2 hours, annealing Process. The temperature and time during the annealing treatment may be appropriately selected from the above ranges in consideration of the alloy composition, plastic working conditions, and the like.
［工程（４）：炉冷工程］
上述した焼鈍処理工程において焼鈍されたＦｅ−Ａｌ合金は、炉冷工程において５５０℃〜６００℃の温度まで炉冷される。炉冷工程における合金の冷却速度については、特に制限されず、焼鈍処理温度や合金の内部歪みの程度等に応じて適宜設定することができる。得られるＦｅ−Ａｌ合金に、強度や制振性等においてより一層優れた特性を備えさせるという観点から、当該焼鈍処理後の合金の冷却は、５５０℃〜６００℃の温度までの温度域における冷却速度を１０℃／分以下（好ましくは１〜５℃／分程度）とすることが望ましい。このような炉冷工程を設けることにより、Ａｌ濃度のゆらぎ（Ａｌ濃度不均衡）を一層増大させることができる。
[Step (4): Furnace cooling step]
The Fe—Al alloy annealed in the above-described annealing process is furnace cooled to a temperature of 550 ° C. to 600 ° C. in the furnace cooling process. The cooling rate of the alloy in the furnace cooling step is not particularly limited, and can be appropriately set according to the annealing temperature, the degree of internal strain of the alloy, and the like. From the viewpoint of providing the obtained Fe-Al alloy with more excellent characteristics in strength, vibration damping and the like, cooling of the alloy after the annealing treatment is performed in a temperature range from 550 ° C to 600 ° C. It is desirable that the speed is 10 ° C./min or less (preferably about 1 to 5 ° C./min). By providing such a furnace cooling step, fluctuations in Al concentration (Al concentration imbalance) can be further increased.
［工程（５）：空冷工程］
上述した炉冷工程において冷却されたＦｅ−Ａｌ合金は、５５０℃〜６００℃の温度から常温の範囲内においては、空冷により冷却される。空冷工程における冷却速度は、送風量を増減する等して調整することができる。また、空冷工程における冷却速度は、外気温等を考慮して適宜変更することとしても良い。
[Step (5): Air cooling step]
The Fe—Al alloy cooled in the furnace cooling step described above is cooled by air cooling in the range from 550 ° C. to 600 ° C. to room temperature. The cooling rate in the air cooling step can be adjusted by increasing / decreasing the amount of blown air. Further, the cooling rate in the air cooling process may be changed as appropriate in consideration of the outside air temperature and the like.
≪本発明のＦｅ−Ａｌ合金の特性について≫
続いて、本発明のＦｅ−Ａｌ合金の特性について説明する。上記の製造方法により製造されるＦｅ−Ａｌ合金は、高い強度を有し、加工性、絶縁性、透磁性、制振性等の特性の点で優れており、種々の分野で応用することができる。本発明のＦｅ−Ａｌ合金は、例えば、その優れた加工性に基づいて、自動車用の高強度材料として有用である。また、本発明のＦｅ−Ａｌ合金は、例えば、その優れた絶縁性に基づいて、モーターのコア材料等に使用される絶縁合金として有用である。さらに、本発明のＦｅ−Ａｌ合金は、例えば、その優れた透磁性に基づいて、各種の電磁材料等に使用される透磁性合金として有用である。また本発明のＦｅ−Ａｌ合金は、熱しやすく冷めにくいという特性を備えており、ＩＨ用の調理器具としても有用である。本発明のＦｅ−Ａｌ合金は、例えば、その優れた制振性に基づいて、自動車の車体材料、軸受け、金型用プレスのシム、工具材、ＤＶＤの筐体、スピーカ部品、精密機器用部材、工具材、制振ブッシュ、スポーツ用具（例えば、テニスのラケットのグリップ等）等に使用される制振合金として有用である。
<< About the characteristics of the Fe-Al alloy of the present invention >>
Then, the characteristic of the Fe-Al alloy of this invention is demonstrated. The Fe—Al alloy produced by the above production method has high strength and is excellent in terms of properties such as workability, insulation, magnetic permeability, vibration damping, and can be applied in various fields. it can. The Fe—Al alloy of the present invention is useful, for example, as a high-strength material for automobiles based on its excellent workability. In addition, the Fe—Al alloy of the present invention is useful as an insulating alloy used for, for example, a motor core material based on its excellent insulating properties. Furthermore, the Fe—Al alloy of the present invention is useful, for example, as a magnetically permeable alloy used for various electromagnetic materials based on its excellent magnetic permeability. Further, the Fe—Al alloy of the present invention has characteristics that it is easy to heat and hard to cool, and is also useful as a cooking utensil for IH. The Fe—Al alloy of the present invention is based on, for example, its excellent vibration damping properties, such as automotive body materials, bearings, mold press shims, tool materials, DVD housings, speaker parts, precision equipment members. It is useful as a damping alloy used for tool materials, damping bushes, sports equipment (eg, tennis racket grips).
本発明のＦｅ−Ａｌ合金は、上記のような特性を有しており、従来報告されているＡｌ含有量１２重量％以下のＦｅ−Ａｌ合金とは異なる特性を有している。具体的には、冷間圧延加工の後に焼鈍処理、及び炉冷処理を行い、さらにその後に空冷処理を行うことにより、合金中にＦｅ３Ａｌ生成前のＡｌ濃度のゆらぎ（Ａｌ濃度不均衡）が生じた状態になっている。このようなＡｌ濃度のゆらぎを有することにより、Ｆｅ−Ａｌ合金は、従来のＡｌ含有量１２重量％以下のＦｅ−Ａｌ合金とは異なる特性を具備していると類推される。 The Fe—Al alloy of the present invention has the characteristics as described above, and has characteristics different from the conventionally reported Fe—Al alloys having an Al content of 12% by weight or less. Specifically, by performing an annealing process and a furnace cooling process after the cold rolling process, and then performing an air cooling process, fluctuations in the Al concentration before the formation of Fe 3 Al in the alloy (Al concentration imbalance) Has occurred. By having such fluctuations in Al concentration, it is presumed that the Fe—Al alloy has different characteristics from the conventional Fe—Al alloy having an Al content of 12% by weight or less.
また、上記の製造方法により得られるＦｅ−Ａｌ合金は、結晶粒子の平均粒径が２５０μｍ以下であり、従来のＦｅ−Ａｌ合金に比べて、結晶粒子径が小さい組織構造を有している。本発明のＦｅ−Ａｌ合金の平均結晶粒子径は、１〜１００μｍの範囲内であることが好ましく、１０〜４０μｍの範囲内であることがさらに好ましい。このような平均粒子径が小さい結晶粒子の組織構造を有することによって、Ｆｅ−Ａｌ合金の強度が高まり、加工性、絶縁性、透磁性、制振性等の特性が一層良好になる。なお、本発明において、Ｆｅ−Ａｌ合金の平均結晶粒径とは、ＪＩＳ Ｇ０５５１に規定されている「鋼のオーステナイト結晶粒度試験方法」に従って測定される値を指す。 Further, the Fe—Al alloy obtained by the above manufacturing method has an average grain size of 250 μm or less, and has a structure having a smaller crystal grain size than a conventional Fe—Al alloy. The average crystal particle diameter of the Fe—Al alloy of the present invention is preferably in the range of 1 to 100 μm, and more preferably in the range of 10 to 40 μm. By having the structure of crystal grains having such a small average particle diameter, the strength of the Fe—Al alloy is increased, and the properties such as workability, insulation, magnetic permeability, and vibration damping are further improved. In the present invention, the average crystal grain size of the Fe—Al alloy refers to a value measured according to the “steel austenite grain size test method” defined in JIS G0551.
本発明のＦｅ−Ａｌ合金の結晶粒子径は、上記の製造方法を構成する工程（２）〜（５）の各工程の実施条件を適宜変更することに調整できる。具体的には、冷間圧延工程における断面減少率を大きくする程、Ｆｅ−Ａｌ合金の結晶粒子の平均粒径が小さくなる。また、焼鈍工程における焼鈍温度を高める程、Ｆｅ−Ａｌ合金の結晶粒子の平均粒径が大きくなる。 The crystal particle diameter of the Fe—Al alloy of the present invention can be adjusted by appropriately changing the implementation conditions of the steps (2) to (5) constituting the production method. Specifically, the average particle size of the crystal grains of the Fe—Al alloy decreases as the cross-sectional reduction rate in the cold rolling process increases. Moreover, the average particle diameter of the crystal grain of a Fe-Al alloy becomes large, so that the annealing temperature in an annealing process is raised.
≪変形例に係る本発明のＦｅ−Ａｌ合金の製造方法について≫
続いて、上述した本実施形態のＦｅ−Ａｌ合金の製造方法の変形例について説明する。変形例に係るＦｅ−Ａｌ合金の製造方法は、上記工程（１）〜（３）を実施した後、工程（４）、（５）に代えて下記工程（６）を実施するものである。すなわち、変形例に係るＦｅ−Ａｌ合金の製造方法においては、工程（１）、工程（２）、工程（３）、及び工程（６）の４工程を経てＦｅ−Ａｌ合金を製造する。換言すれば、変形例に係るＦｅ−Ａｌ合金の製造方法においては、上記工程（４）の焼鈍処理工程を省略し、工程（５）に代えて空冷の開始温度を焼鈍処理工程における焼鈍温度とした工程（工程（６））を設けたものと言える。以下、工程（６）について説明する。
<< About the manufacturing method of the Fe-Al alloy of this invention which concerns on a modification >>
Then, the modification of the manufacturing method of the Fe-Al alloy of this embodiment mentioned above is demonstrated. The manufacturing method of the Fe-Al alloy which concerns on a modification implements the following process (6) instead of process (4), (5), after implementing said process (1)-(3). That is, in the Fe—Al alloy manufacturing method according to the modification, the Fe—Al alloy is manufactured through the four steps of step (1), step (2), step (3), and step (6). In other words, in the manufacturing method of the Fe—Al alloy according to the modification, the annealing process step of the above step (4) is omitted, and the air cooling start temperature is replaced with the annealing temperature in the annealing process step instead of the step (5). It can be said that this step (step (6)) was provided. Hereinafter, the step (6) will be described.
［工程（６）：空冷工程］
工程（６）においては、上述した工程（３）の焼鈍処理工程において焼鈍処理されたＦｅ−Ａｌ合金を焼鈍処理温度、すなわち磁気変態点（６８７℃）以上であって、１０００℃（好ましくは８５０℃）以下の温度から空冷により冷却される。工程（６）における冷却速度は、上記工程（５）の場合と同様に送風量を増減する等して調整することができる。また、工程（６）における冷却速度は、外気温等を考慮して適宜変更することとしても良い。
[Step (6): Air cooling step]
In step (6), annealing temperature annealing-treated Fe-Al alloy in the annealing process of the above-described steps (3), namely a a magnetic variable state point (687 ° C.) or higher, 1000 ° C. (preferably It is cooled by air cooling from a temperature of 850 ° C. or lower. The cooling rate in the step (6) can be adjusted by increasing / decreasing the amount of blown air as in the case of the step (5). Further, the cooling rate in the step (6) may be appropriately changed in consideration of the outside air temperature and the like.
≪変形例に係る本発明の製造方法により製造されたＦｅ−Ａｌ合金の特性について≫
本変形例に係るＦｅ−Ａｌ合金の製造方法のように、工程（３）の焼鈍処理工程の後に常温まで空冷したものについても、従来報告されているＡｌ含有量１２重量％以下のＦｅ−Ａｌ合金とは異なる特性を有している。具体的には、冷間圧延加工の後に焼鈍処理を行い、さらにその後に空冷処理を行うことにより、合金中にＦｅ３Ａｌ生成前のＡｌ濃度のゆらぎ（Ａｌ濃度不均衡）が生じた状態になっている。このようなＡｌ濃度のゆらぎを有することにより、制振性の面において優れた特性を示す。
<< About the characteristic of the Fe-Al alloy manufactured with the manufacturing method of this invention which concerns on a modification >>
As in the method for producing an Fe—Al alloy according to this modification, the conventionally reported Fe—Al having an Al content of 12% by weight or less is also used for those that are air-cooled to room temperature after the annealing treatment step (3). It has different properties from alloys. Specifically, by performing an annealing process after the cold rolling process and then performing an air cooling process, fluctuations in Al concentration before the formation of Fe 3 Al (Al concentration imbalance) occurred in the alloy. It has become. By having such an Al concentration fluctuation, excellent characteristics in terms of damping properties are exhibited.
上記の製造方法により製造されるＦｅ−Ａｌ合金についても、高強度かつ制振性の面においても優れた性能を示す。加えて、加工性、絶縁性、透磁性等の特性においても優れており、種々の分野で応用することができる。本発明のＦｅ−Ａｌ合金は、自動車用の高強度材料、モーターのコア材料等に使用される絶縁合金、各種の電磁材料等に使用される透磁性合金、ＩＨ用の調理器具、自動車の車体材料、軸受け、金型用プレスのシム、工具材、ＤＶＤの筐体、スピーカ部品、精密機器用部材、工具材、制振ブッシュ、スポーツ用具（例えば、テニスのラケットのグリップ等）等、様々な用途において利用することができる。 The Fe—Al alloy produced by the above production method also exhibits excellent performance in terms of high strength and vibration damping. In addition, it is excellent in properties such as workability, insulation, and magnetic permeability, and can be applied in various fields. The Fe—Al alloy of the present invention is a high-strength material for automobiles, an insulating alloy used for a motor core material, a magnetically permeable alloy used for various electromagnetic materials, an IH cooking appliance, an automobile body, etc. Various materials, bearings, die press shims, tool materials, DVD housings, speaker parts, precision equipment members, tool materials, vibration control bushes, sports equipment (eg tennis racket grips) It can be used in applications.
また、変形例に係る製造方法により得られるＦｅ−Ａｌ合金についても、結晶粒子の平均粒径が２５０μｍ以下であり、従来のＦｅ−Ａｌ合金に比べて、結晶粒子径が小さい組織構造を有している。このＦｅ−Ａｌ合金の平均結晶粒子径は、１〜１００μｍの範囲内であることが好ましく、１０〜４０μｍの範囲内であることがさらに好ましい。このような平均粒子径が小さい結晶粒子の組織構造を有することによって、Ｆｅ−Ａｌ合金の強度が高まり、加工性、絶縁性、透磁性、制振性等の特性が一層良好になる。 In addition, the Fe—Al alloy obtained by the production method according to the modification also has an average grain size of 250 μm or less, and has a structure with a smaller crystal grain size than a conventional Fe—Al alloy. ing. The average crystal particle diameter of this Fe—Al alloy is preferably in the range of 1 to 100 μm, and more preferably in the range of 10 to 40 μm. By having the structure of crystal grains having such a small average particle diameter, the strength of the Fe—Al alloy is increased, and the properties such as workability, insulation, magnetic permeability, and vibration damping are further improved.
本発明のＦｅ−Ａｌ合金の結晶粒子径は、上記の製造方法を構成する各工程の実施条件を適宜変更することに調整できる。具体的には、冷間圧延工程における断面減少率を大きくする程、Ｆｅ−Ａｌ合金の結晶粒子の平均粒径が小さくなる。また、焼鈍工程における焼鈍温度を高める程、Ｆｅ−Ａｌ合金の結晶粒子の平均粒径が大きくなる。 The crystal particle diameter of the Fe—Al alloy of the present invention can be adjusted by appropriately changing the implementation conditions of each step constituting the production method. Specifically, the average particle size of the crystal grains of the Fe—Al alloy decreases as the cross-sectional reduction rate in the cold rolling process increases. Moreover, the average particle diameter of the crystal grain of a Fe-Al alloy becomes large, so that the annealing temperature in an annealing process is raised.
≪本発明のＦｅ−Ａｌ合金の結晶構造解析等の結果について≫
Ａｌ濃度の不均一な、いわゆる「ゆらぎ」の存在を明確にするには、熱処理によって「ゆらぎ」が起こっていること、及び「ゆらぎ」からＦｅ３Ａｌに変態していることの確認が必要である。かかる知見の下、構造解析のためのＸ線による結晶構造解析、及びミラー指数の解析のためのＴＥＭ観察を行った。以下、それぞれの結果について説明する。
<< Results of Crystal Structure Analysis of Fe-Al Alloy of the Present Invention >>
In order to clarify the existence of so-called “fluctuation” with non-uniform Al concentration, it is necessary to confirm that “fluctuation” has occurred by heat treatment and that “fluctuation” has transformed into Fe 3 Al. is there. Under such knowledge, crystal structure analysis by X-ray for structural analysis and TEM observation for Miller index analysis were performed. Hereinafter, each result will be described.
先ず、上記の製造方法により作成したＦｅ−Ａｌ合金について結晶構造解析を行った結果について説明する。なお、本結晶構造解析においては、測定装置として「Ｓｍａｒｔ Ｌａｂ Ｇｕｉｄａｎｃｅ」（株式会社 リガク製）を用い、簡易広角集中法によりＸ線回折測定を行った。 First, the results of the crystal structure analysis of the Fe—Al alloy prepared by the above manufacturing method will be described. In this crystal structure analysis, “Smart Lab Guidance” (manufactured by Rigaku Corporation) was used as a measuring device, and X-ray diffraction measurement was performed by a simple wide-angle concentration method.
上述した方法により本発明のＦｅ−Ａｌ合金についてＸ線回折測定したところ、図１及び図２に示すようなＸ線回折像が得られた。このＸ線回折像を解析したところ、Ｆｅ３Ａｌ、ＦｅＡｌ、及びα−Ｆｅのピークが確認された。また、これに加えて、図１中に丸印を付して示すように、Ｆｅ３Ａｌ、ＦｅＡｌ、及びα−Ｆｅとは異なるミラー指数を有するピークが確認された。このピークは、Ｆｅ３Ａｌの（２２０）面近傍に発現している。また、Ｆｅ１３Ａｌ３は、Ｆｅ３Ａｌと組成比が近いことから、結晶構造についてもＦｅ３Ａｌと近似している。これらの観点から、図１及び図２において丸印を付したピークは、Ｆｅ１３Ａｌ３によるものであると考えられる。 When the X-ray diffraction measurement was performed on the Fe—Al alloy of the present invention by the method described above, X-ray diffraction images as shown in FIGS. 1 and 2 were obtained. When this X-ray diffraction image was analyzed, peaks of Fe 3 Al, FeAl, and α-Fe were confirmed. In addition to this, as shown with a circle in FIG. 1, a peak having a Miller index different from that of Fe 3 Al, FeAl, and α-Fe was confirmed. This peak appears in the vicinity of the (220) plane of Fe 3 Al. Further, Fe 13 Al 3, since Fe 3 Al composition ratio is close approximates a Fe 3 Al also crystal structure. From these viewpoints, the peaks marked in FIG. 1 and FIG. 2 are considered to be due to Fe 13 Al 3 .
また、図４に示す本発明のＦｅ−Ａｌ合金に係る＜００１＞入射の電子回折像により、Ｆｅ３Ａｌの生成が確認された。 In addition, the Fe-Al according to the alloy <001> electron diffraction image of the incident of the present invention shown in FIG. 4, Fe 3 Al generation of was confirmed.
上述したように、本発明のＦｅ−Ａｌ合金は、α−ＦｅやＦｅＡｌだけでなく、Ｆｅ３ＡｌやＦｅ１３Ａｌ３が混在したものである。また、α−Ｆｅ、ＦｅＡｌ、Ｆｅ３Ａｌ、及びＦｅ１３Ａｌ３においてＡｌの配列が相違している。そのため、本発明のＦｅ−Ａｌ合金は、Ａｌ濃度が不均一、すなわちＡｌ濃度のゆらぎを有することがわかる。 As described above, the Fe—Al alloy of the present invention is a mixture of not only α-Fe and FeAl but also Fe 3 Al and Fe 13 Al 3 . In addition, the arrangement of Al is different in α-Fe, FeAl, Fe 3 Al, and Fe 13 Al 3 . Therefore, it can be seen that the Fe—Al alloy of the present invention has a non-uniform Al concentration, that is, fluctuations in the Al concentration.
なお、上述した変形例に係る本発明のＦｅ−Ａｌ合金の製造方法により製造したＦｅ−Ａｌ合金についてのＸ線回折像及び電子回折像も同様のものであった。従って、変形例に係る製造方法によって製造されたＦｅ−Ａｌ合金についても、α−ＦｅやＦｅＡｌだけでなく、Ｆｅ３ＡｌやＦｅ１３Ａｌ３が混在したものであり、Ａｌ濃度が不均一、すなわちＡｌ濃度のゆらぎを有するものであった。 In addition, the X-ray diffraction image and the electron diffraction image about the Fe-Al alloy manufactured by the manufacturing method of the Fe-Al alloy of this invention which concerns on the modification mentioned above were also the same. Therefore, not only α-Fe and FeAl but also Fe 3 Al and Fe 13 Al 3 are mixed in the Fe—Al alloy manufactured by the manufacturing method according to the modified example, and the Al concentration is non-uniform, that is, It had a fluctuation of the Al concentration.
≪空冷工程の開始温度が制振性に与える影響について≫
上述した製造方法において、空冷工程の開始温度が制振性に与える影響について検討した実験結果について説明する。本実験例においては、サンプルＡ，Ｂ，Ｃからなる３種類のＦｅ−Ａｌ合金を製造した。サンプルＡは、上記変形例に係るＦｅ−Ａｌ合金の製造方法により製造したサンプルである。サンプルＡは、工程（６）における空冷開始温度を７５０℃として製造された。サンプルＢ及びサンプルＣは、上記Ｆｅ−Ａｌ合金の製造方法（工程（１）〜工程（５））により製造された。サンプルＢは、工程（５）における空冷開始温度を６００℃として空冷することにより製造された。また、サンプルＣは、工程（５）において空冷開始温度を３００℃として空冷することにより製造された。サンプルＡ，Ｂ，Ｃは、それぞれ短冊状（１ｔ×２０×３００）に成形した。制振性能に関する試験は、共振法により行なった。
≪Effect of start temperature of air cooling process on damping performance≫
In the manufacturing method described above, the experimental results of examining the influence of the start temperature of the air cooling process on the vibration damping properties will be described. In this experimental example, three types of Fe—Al alloys consisting of samples A, B, and C were manufactured. Sample A is a sample manufactured by the method for manufacturing an Fe—Al alloy according to the modification. Sample A was produced by setting the air cooling start temperature in step (6) to 750 ° C. Sample B and Sample C were manufactured by the above-described Fe—Al alloy manufacturing method (step (1) to step (5)). Sample B was manufactured by air cooling with the air cooling start temperature in step (5) set to 600 ° C. Sample C was manufactured by air-cooling with the air-cooling start temperature being 300 ° C. in step (5). Samples A, B, and C were each formed into a strip shape (1 t × 20 × 300). The test on the vibration damping performance was performed by the resonance method.
上述したサンプルＡ，Ｂ，Ｃについて、ひずみ振幅［％］と、損失係数ηとの関係を調べた。その結果を下記表１に示す。 Regarding the samples A, B, and C described above, the relationship between the strain amplitude [%] and the loss coefficient η was examined. The results are shown in Table 1 below.
上記表１に示すように、上記工程（１）〜（５）の製造工程に則り、空冷開始温度を６００℃として空冷工程を開始したサンプルＢは、ひずみ振幅の条件によらず損失係数ηが高い値を示した。また、上記工程（１），（２），（３）及び（６）の製造工程を経て作成された空冷開始温度が７５０℃であるサンプルＡについても、損失係数ηがサンプルＢに匹敵する程度に高い値を示した。一方、空冷開始温度が３００℃であるサンプルＣについては、ひずみ振幅の条件によらず他のサンプルＡ，Ｂに比べて損失係数ηが低かった。このように、本発明の製造条件に合致した空冷開始温度から空冷を開始することにより、制振性を向上させうることが判明した。 As shown in Table 1 above, sample B, which started the air cooling step with the air cooling start temperature set at 600 ° C. in accordance with the manufacturing steps of the above steps (1) to (5), has a loss coefficient η regardless of the strain amplitude condition. High value was shown. Further, the loss coefficient η is comparable to that of the sample B for the sample A having the air cooling start temperature of 750 ° C. produced through the manufacturing steps of the above steps (1), (2), (3) and (6). Showed a high value. On the other hand, the loss coefficient η of the sample C whose air cooling start temperature is 300 ° C. is lower than that of the other samples A and B regardless of the strain amplitude condition. As described above, it has been found that the damping performance can be improved by starting the air cooling from the air cooling start temperature that matches the production conditions of the present invention.
本発明によれば、Ａｌ含有量を６〜１２重量％にしつつ、Ａｌ濃度のゆらぎを有するＦｅ−Ａｌ合金を提供することができる。これにより、制振性及び強度面の双方の観点から実用性に優れたＦｅ−Ａｌ合金を提供でき、例えば自動車の車体材料、軸受け、金型用プレスのシム、工具材、ＤＶＤの筐体、スピーカ部品、精密機器用部材、工具材、制振ブッシュ、スポーツ用具（例えば、テニスのラケットのグリップ等）等のような制振性が求められる多岐の分野において有効利用可能である。 According to the present invention, it is possible to provide an Fe—Al alloy having Al concentration fluctuation while the Al content is 6 to 12% by weight. Thereby, it is possible to provide an Fe-Al alloy that is excellent in practicality from the viewpoint of both vibration damping and strength, such as automobile body materials, bearings, shims for mold presses, tool materials, DVD housings, The present invention can be effectively used in various fields where vibration damping is required, such as speaker parts, precision equipment members, tool materials, vibration damping bushes, sports equipment (for example, tennis racket grips).
Claims (1)
（１） Ａｌ含有量６〜１２重量％、残部Ｆｅ及び不可避的不純物からなる合金を熱間加工により塑性加工する塑性加工工程。
（２） 塑性加工した合金を冷間圧延加工する冷間圧延工程。
（３） 冷間圧延加工後の合金を磁気変態点以上であって、１０００℃以下の温度で焼鈍する焼鈍処理工程。
（４） 焼鈍処理工程の後、常温まで空冷する空冷工程。
Look including the following steps, the production method of the Fe-Al alloy having a fluctuation of the Al concentration.
(1) A plastic working step of plastic working an alloy comprising Al content of 6 to 12% by weight, the balance Fe and inevitable impurities by hot working.
(2) A cold rolling process in which a plastically worked alloy is cold rolled.
(3) the cold rolling process after the alloy comprising at least a magnetic variable state point, annealing step of annealing at 1000 ° C. or lower.
(4) An air-cooling process in which air is cooled to room temperature after the annealing process.
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