JP2010227964A - Method for producing metal material and metal material - Google Patents
Method for producing metal material and metal material Download PDFInfo
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Abstract
【課題】金属母材の所望の部位を所望の組成の金属とすることが可能な金属材の製造方法及びこの方法で製造された金属材を提供する。
【解決手段】金属母材１ａ，１ｂとは異なる組成であり、且つ金属母材１ａ，１ｂとの化学反応を生じる添加材１０を、金属母材１ａ，１ｂの一部である攪拌部２０に配置し、攪拌部２０に棒状の回転ツール１００の先端を当接させつつ回転させる。これにより、摩擦攪拌接合の手法を利用した一つの方法で、金属母材１ａ，１ｂの所望の部位に対して添加材１０の分散、拡散及び析出あるいは分散、拡散及び変態といった合金を製造する３つの過程を実現することができる。そのため、金属母材１ａ，１ｂの所望の部位を所望の組成の金属とすることが可能となる。
【選択図】図３The present invention provides a method for producing a metal material capable of making a desired part of a metal base material a metal having a desired composition, and a metal material produced by this method.
An additive 10 having a composition different from that of metal base materials 1a and 1b and causing a chemical reaction with the metal base materials 1a and 1b is applied to a stirring unit 20 which is a part of the metal base materials 1a and 1b. It arrange | positions and it rotates, making the front-end | tip of the rod-shaped rotation tool 100 contact the stirring part 20. FIG. Thus, an alloy such as dispersion, diffusion and precipitation or dispersion, diffusion and transformation of the additive 10 is produced at a desired portion of the metal base materials 1a and 1b by one method using a friction stir welding method. One process can be realized. Therefore, it becomes possible to make a desired portion of the metal base materials 1a and 1b a metal having a desired composition.
[Selection] Figure 3
Description
本発明は、金属材の製造方法及び金属材に関し、特に、回転ツールの先端を金属材に当接させつつ回転させる工程を含む金属材の製造方法及び当該製造方法により製造された金属材に関する。 The present invention relates to a method for manufacturing a metal material and a metal material, and more particularly, to a method for manufacturing a metal material including a step of rotating a tip of a rotating tool while contacting the metal material, and a metal material manufactured by the manufacturing method.
近年、金属材料からなる被接合材同士を接合する摩擦攪拌接合が注目されている。この摩擦攪拌接合は、板状の被接合材の端部同士を突き合わせて接合部とし、当該接合部に棒状の回転ツールの先端を挿入して、回転ツールを回転させつつ接合部に沿って移動させることにより被接合材の接合を行う。このような摩擦攪拌接合では、鉄道車両や船舶といった大型構造物や突き合わせ部が長い板材などに適用する場合ギャップ（表面割れ状欠陥部）が発生してしまうことがある。ギャップとは被接合材の突き合わせ部の不整合により生じる隙間のことを指す。突き合わせ部に発生するギャップは接合部の欠陥の原因となるため突き合わせ部を平滑にする等の対策を講じて抑制する必要がある。 In recent years, friction stir welding for joining materials to be joined made of metal materials has attracted attention. In this friction stir welding, the ends of the plate-shaped workpieces are brought into contact with each other to form a joint, and the tip of a rod-shaped rotary tool is inserted into the joint and moved along the joint while rotating the rotary tool. To join the materials to be joined. In such friction stir welding, a gap (surface crack-like defect portion) may occur when applied to a large structure such as a railway vehicle or a ship or a plate material having a long butted portion. The gap refers to a gap that is generated due to a mismatch between the butted portions of the materials to be joined. Since the gap generated in the butt portion causes a defect in the joint portion, it is necessary to suppress the gap by smoothing the butt portion.
そこで、例えば、特許文献１では、表面割れ状欠陥部が生じた被補修材の表面割れ状欠陥部に被補修材と同じ組成の粉末状接合材料を充填し、接合工具（回転ツール）を被補修材の表面割れ状欠陥部に挿入して回転させつつ表面割れ状欠陥部に沿って移動させることにより、被補修材の表面割れ状欠陥部を補修する技術が開示されている。 Therefore, for example, in Patent Document 1, the surface cracked defect portion of the repaired material in which the surface cracked defect portion is generated is filled with a powdery bonding material having the same composition as the repaired material, and the bonding tool (rotary tool) is covered. A technique for repairing a surface crack-like defect portion of a repaired material by inserting it into a surface crack-like defect portion of a repair material and moving it along the surface crack-like defect portion while rotating is disclosed.
ところで、アルミニウム（Ａｌ）と銅（Ｃｕ）とを主成分とする合金であるジュラルミンや、鉄（Ｆｅ）と炭素（Ｃ）との合金である炭素鋼等の金属母材に金属母材とは異なる組成の物質を添加して合金を製造することが行われている。ジュラルミンや高炭素鋼は優れた強度を有するが、硬いため加工が難しいことが欠点である。特に、ジュラルミンや高炭素鋼で大きな構造物を製造する場合、構造物の全ての部位にジュラルミンや高炭素鋼の大きな強度や硬度は必ずしも必要とはされず、構造物の一部の摺動面等の強度や硬度が大きければ足りる。そのため、ジュラルミンや高炭素鋼で構造物を製造する場合、強度や硬度が必要とされない箇所もジュラルミンや高炭素鋼等の硬く加工が難しい金属材を加工して製造することになり、製造労力の軽減の見地から改善が強く望まれている。 By the way, what is a metal base material to a metal base material such as duralumin which is an alloy mainly composed of aluminum (Al) and copper (Cu) and carbon steel which is an alloy of iron (Fe) and carbon (C)? An alloy is manufactured by adding substances having different compositions. Duralumin and high carbon steel have excellent strength, but they are hard and difficult to work. In particular, when manufacturing a large structure with duralumin or high carbon steel, the large strength or hardness of duralumin or high carbon steel is not necessarily required for all parts of the structure. It is sufficient if the strength and hardness of the material are large. Therefore, when manufacturing structures with duralumin or high carbon steel, parts that do not require strength or hardness will be manufactured by processing hard and difficult-to-work metal materials such as duralumin and high carbon steel. Improvement is strongly desired from the viewpoint of mitigation.
本発明は、このような実情に考慮してなされたものであり、その目的は、金属母材の所望の部位を所望の組成の金属とすることが可能な金属材の製造方法及びこの方法で製造された金属材を提供することにある。 The present invention has been made in view of such circumstances, and an object of the present invention is to provide a method for producing a metal material capable of making a desired portion of a metal base material a metal having a desired composition, and this method. It is to provide a manufactured metal material.
本発明は、金属母材を用意する工程と、金属母材とは異なる組成であり、且つ金属母材との化学反応を生じる添加材を、金属母材の一部である攪拌部に配置する工程と、攪拌部に棒状の回転ツールの先端を当接させつつ回転させる工程とを含む金属材の製造方法である。 In the present invention, a step of preparing a metal base material and an additive that has a composition different from that of the metal base material and causes a chemical reaction with the metal base material are disposed in a stirring portion that is a part of the metal base material. It is a manufacturing method of a metal material including a step and a step of rotating while a tip of a rod-shaped rotating tool is brought into contact with the stirring portion.
この構成によれば、金属母材とは異なる組成であり、且つ金属母材との化学反応を生じる添加材を、金属母材の一部である攪拌部に配置し、攪拌部に棒状の回転ツールの先端を当接させつつ回転させるため、摩擦攪拌接合の手法を利用した一つの方法で、金属母材の所望の部位に対して添加材の分散、拡散、析出あるいは分散、拡散、変態といった合金を製造する３つの過程を実現することができる。そのため、金属母材の所望の部位を所望の組成の金属とすることが可能となる。なお、例えば、上記「化学反応」とは、金属母材と添加材との界面に生成物が生成する事、添加材が金属母材中に固溶、析出及び変態の少なくともいずれかをする事、並びに金属母材が添加材中に固溶、析出及び変態の少なくともいずれかをする事等を指すものとする。また、添加材を金属母材の一部である攪拌部に配置する工程では、金属母材中に凹部を設け、当該凹部に添加材を配置する態様、金属母材同士を近接させて、その間に添加材を配置する態様、及び板状の金属母材同士を重ね合わせ、その間に添加材を配置する重ね合わせ接合と類似の態様のいずれも含むものとする。さらに、攪拌部に棒状の回転ツールの先端を当接させつつ回転させる工程では、回転ツールの移動を伴わないスポット型の摩擦攪拌処理も含まれるものとする。 According to this configuration, the additive having a composition different from that of the metal base material and causing a chemical reaction with the metal base material is disposed in the stirring portion that is a part of the metal base material, and the rod-like rotation is provided in the stirring portion. In order to rotate while abutting the tip of the tool, one method using the friction stir welding method, such as dispersion, diffusion, precipitation or dispersion, diffusion, transformation of the additive to the desired part of the metal base material Three processes for producing the alloy can be realized. Therefore, a desired part of the metal base material can be a metal having a desired composition. For example, the above “chemical reaction” means that a product is generated at the interface between the metal matrix and the additive, and that the additive is at least one of solid solution, precipitation and transformation in the metal matrix. In addition, the metal base material indicates at least one of solid solution, precipitation, and transformation in the additive material. Further, in the step of arranging the additive in the stirring part which is a part of the metal base material, a recess is provided in the metal base material, the mode of arranging the additive in the concave part, the metal base materials are brought close to each other, In addition, both the aspect in which the additive is disposed and the aspect similar to the superposition joining in which the plate-like metal base materials are overlapped and the additive is disposed therebetween are included. Furthermore, the step of rotating the agitating portion while bringing the tip of the rod-shaped rotating tool into contact includes a spot type friction agitating process that does not involve the movement of the rotating tool.
この場合、攪拌部に棒状の回転ツールを当接させつつ回転させる工程では、金属母材中に添加材を攪拌、拡散、及び析出させることが好適である。 In this case, it is preferable to stir, diffuse, and precipitate the additive in the metal base material in the step of rotating the bar-shaped rotating tool in contact with the stirring unit.
この構成によれば、金属母材中に添加材を攪拌、拡散、及び析出させることにより、特に金属母材がＡｌであり、添加材がＣｕである場合に、金属母材の所望の部位をさらに優れた特性の金属とすることが可能となる。 According to this configuration, by stirring, diffusing, and precipitating the additive in the metal base material, particularly when the metal base material is Al and the additive material is Cu, a desired portion of the metal base material is obtained. Furthermore, it is possible to obtain a metal having excellent characteristics.
あるいは、攪拌部に棒状の回転ツールを当接させつつ回転させる工程では、金属母材中に添加材を攪拌、拡散、及び変態させることが好適である。 Alternatively, in the step of rotating while a rod-shaped rotating tool is brought into contact with the stirring portion, it is preferable to stir, diffuse, and transform the additive in the metal base material.
この構成によれば、金属母材中に添加材を攪拌、拡散、及び変態させることにより、特に金属母材がＦｅであり、添加材がＣである場合に、金属母材の所望の部位をさらに優れた特性の金属とすることが可能となる。 According to this configuration, by stirring, diffusing, and transforming the additive in the metal base material, particularly when the metal base material is Fe and the additive material is C, a desired portion of the metal base material is obtained. Furthermore, it is possible to obtain a metal having excellent characteristics.
この場合、金属母材はＡｌを含むものとし、添加材はＣｕを含むものとすることが好適である。 In this case, it is preferable that the metal base material contains Al and the additive material contains Cu.
この構成によれば、金属母材はＡｌを含むものとし、添加材はＣｕを含むものとするため、ＡｌとＣｕとの合金であるジュラルミンを金属母材の所望の部位に製造することが可能となる。 According to this configuration, since the metal base material includes Al and the additive material includes Cu, duralumin, which is an alloy of Al and Cu, can be manufactured at a desired portion of the metal base material.
また、攪拌部に棒状の回転ツールを当接させつつ回転させる工程では、攪拌部に回転ツールを少なくとも２回通過させることが好適である。 Further, in the step of rotating the agitating portion while bringing the rod-like rotating tool into contact therewith, it is preferable to pass the rotating tool through the agitating portion at least twice.
この構成によれば、攪拌部に回転ツールを少なくとも２回通過させるため、攪拌部の状態をより良好なものとすることができる。 According to this configuration, since the rotary tool is passed at least twice through the stirring unit, the state of the stirring unit can be improved.
また、攪拌部は、金属母材の表面に対して幅ｗの凹部であり、回転ツールの先端の中央部は突出したプローブであり、プローブの径ｒは、ｒ≧２ｗとすることが好適である。 Further, the stirring portion is a concave portion having a width w with respect to the surface of the metal base material, the center portion of the tip of the rotary tool is a protruding probe, and the probe diameter r is preferably r ≧ 2w. is there.
この構成によれば、回転ツールのプローブの径ｒが攪拌部の幅ｗに対して十分に大きいため、攪拌部の状態をより良好なものとすることができる。なお、ここで、「金属母材の表面に対して幅ｗの凹部」とは、金属母材が一体の部材でその表面の凹部が幅ｗである他、金属部材が２個以上の部材であり、その２個以上の金属母材の距離が金属母材の表面でｗである場合も含むものとする。 According to this configuration, since the diameter r of the probe of the rotary tool is sufficiently larger than the width w of the stirring unit, the state of the stirring unit can be made better. Here, the “concave portion having a width w with respect to the surface of the metal base material” means that the metal base material is an integral member and the concave portion on the surface has a width w, and that the metal member is two or more members. Yes, including the case where the distance between the two or more metal base materials is w on the surface of the metal base material.
また、添加材を金属母材の攪拌部に配置する工程では、攪拌部に金属母材及び添加材とは異なる物質を少なくとも１種類以上さらに配置するものとできる。 Further, in the step of arranging the additive in the stirring portion of the metal base material, at least one or more substances different from the metal base material and the additive material may be further placed in the stirring portion.
本発明においては、金属母材と添加材との２種類の物質からなる金属材のみならず、３種類以上の物質からなる金属材も製造することが可能である。 In the present invention, it is possible to produce not only a metal material composed of two kinds of materials, a metal base material and an additive material, but also a metal material composed of three or more kinds of materials.
また、添加材を金属母材の攪拌部に配置する工程では、粉状、粒状及び板状のいずれかの添加材を攪拌部に配置することが好適である。 In addition, in the step of placing the additive in the stirring portion of the metal base material, it is preferable to place any one of powdery, granular, and plate-like additives in the stirring portion.
この構成によれば、粉状、粒状及び板状のいずれかの添加材を攪拌部に配置するため、攪拌部において製造される金属材の組成を制御することがより容易になる。 According to this configuration, since any one of powdery, granular, and plate-like additives is disposed in the stirring part, it is easier to control the composition of the metal material produced in the stirring part.
この場合、粉状又は粒状の添加材は複数の種類の粉状又は粒状の物質の混合物及び複数種類の板状の物質の積層物からなるものとし、複数の種類の物質の割合を変更することにより、製造される金属材の性質を変更することが好適である。 In this case, the powdery or granular additive shall consist of a mixture of a plurality of types of powdery or granular substances and a laminate of a plurality of types of plate-like substances, and change the ratio of the plurality of types of substances. Thus, it is preferable to change the properties of the metal material to be manufactured.
この構成によれば、粉状又は粒状の添加材は複数の種類の粉状又は粒状の物質の混合物及び複数種類の板状の物質の積層物からなるものとし、複数の種類の物質の割合を変更することにより、製造される金属材の性質を変更するため、攪拌部において製造される金属材の組成を制御することがさらに容易になり、所望の性質の金属材を製造することがさらに容易となる。 According to this configuration, the powdery or granular additive material is composed of a mixture of a plurality of kinds of powdery or granular substances and a laminate of a plurality of kinds of plate-like substances, and the ratio of the plurality of kinds of substances is determined. By changing the properties of the metal material to be produced, it becomes easier to control the composition of the metal material produced in the stirring unit, and it is even easier to produce a metal material having a desired property. It becomes.
一方、添加材を金属母材の攪拌部に配置する工程では、添加材の端部を金属母材に対して当接又は近接させて、添加材の端部を当接又は近接させた箇所を攪拌部とし、攪拌部に棒状の回転ツールを当接させつつ回転させる工程では、攪拌部に回転ツールを当接させつつ回転させることにより、金属母材と添加材とを接合することが好適である。 On the other hand, in the step of placing the additive in the stirring portion of the metal base, the end of the additive is brought into contact with or close to the metal base, and the end where the end of the additive is brought into contact or close In the step of rotating the agitating portion while a rod-shaped rotating tool is in contact with the agitating portion, it is preferable to join the metal base material and the additive by rotating the agitating portion while abutting the rotating tool. is there.
この構成によれば、添加材の端部を金属母材に対して当接又は近接させて、添加材の端部を当接又は近接させた箇所を攪拌部とし、攪拌部に回転ツールを当接させつつ回転させることにより、金属母材と添加材とを接合するため、金属母材と添加材とを接合させた上で、金属母材と添加材との接合部となる攪拌部を所望の組成の金属材とすることが可能となる。なお、この場合、添加材を金属母材の一部である攪拌部に配置する工程では、金属母材同士を近接させて、その間に添加材を配置する態様、及び板状の金属母材同士を重ね合わせ、その間に添加材を配置する重ね合わせ接合と類似の態様のいずれも含むものとする。さらに、攪拌部に棒状の回転ツールの先端を当接させつつ回転させる工程では、回転ツールの移動を伴わないスポット型の摩擦攪拌処理も含まれるものとする。 According to this configuration, the end of the additive is brought into contact with or close to the metal base material, the portion where the end of the additive is brought into contact with or close to is used as the stirring unit, and the rotating tool is applied to the stirring unit. Since the metal base material and the additive material are joined by rotating while being in contact with each other, the metal base material and the additive material are joined together, and then a stirring portion that serves as a joint portion between the metal base material and the additive material is desired. It becomes possible to set it as the metal material of the composition. In this case, in the step of arranging the additive in the stirring portion that is a part of the metal base material, the metal base materials are brought close to each other, and the additive material is placed between them, and the plate-shaped metal base materials These are both included in a manner similar to the superposition joining in which the additive materials are placed between them. Furthermore, the step of rotating the agitating portion while bringing the tip of the rod-shaped rotating tool into contact includes a spot type friction agitating process that does not involve the movement of the rotating tool.
この場合、添加材を金属母材の攪拌部に配置する工程では、添加材及び金属母材の両方の組成を含む中間材を添加材と金属母材との間に配置し、中間材を配置した箇所を攪拌部とすることが好適である。 In this case, in the step of placing the additive in the stirring portion of the metal base material, an intermediate material including the composition of both the additive material and the metal base material is placed between the additive material and the metal base material, and the intermediate material is placed. It is suitable to make the done part into a stirring part.
この構成によれば、添加材及び金属母材の両方の組成を含む中間材を添加材と金属母材との間に配置し、中間材を配置した箇所を攪拌部とするため、金属母材と中間材との生成物及び添加材と中間材との生成物が厚く生成されることが抑制されるため、より良好な攪拌部とすることが可能となる。 According to this configuration, the intermediate material including the composition of both the additive material and the metal base material is disposed between the additive material and the metal base material, and the portion where the intermediate material is disposed is used as the stirring portion. Since it is suppressed that the product of an intermediate material and the product of an additive material and an intermediate material are produced | generated thickly, it becomes possible to set it as a more favorable stirring part.
加えて、本発明は、本発明の金属材の製造方法によって製造された金属材である。 In addition, this invention is the metal material manufactured by the manufacturing method of the metal material of this invention.
この構成によれば、所望の部位が所望の組成の金属である金属材とできる。 According to this configuration, a desired material can be a metal material having a desired composition.
本発明の金属材の製造方法及び金属材によれば、金属母材の所望の部位を所望の組成の金属とすることが可能となる。 According to the method for producing a metal material and the metal material of the present invention, a desired portion of the metal base material can be made a metal having a desired composition.
以下、本発明の実施の形態について添付図面を参照して説明する。本実施形態では、図１に示すような回転ツール１００を用意する。回転ツール１００は、略円筒状をなし、先端のショルダー１０１より小径の略円柱状のプローブ１０２を備えている。回転ツール１００の材質は、例えば、ＪＩＳに規格されているＳＫＤ６１鋼等の工具鋼や、タングステンカーバイト（ＷＣ）を主成分とする超硬合金、またはＳｉ３Ｎ４等のセラミックスからなるものとすることができる。 Embodiments of the present invention will be described below with reference to the accompanying drawings. In this embodiment, a rotating tool 100 as shown in FIG. 1 is prepared. The rotary tool 100 has a substantially cylindrical shape, and includes a substantially cylindrical probe 102 having a smaller diameter than the shoulder 101 at the tip. The material of the rotary tool 100 is made of, for example, a tool steel such as SKD61 steel standardized by JIS, a cemented carbide containing tungsten carbide (WC) as a main component, or a ceramic such as Si 3 N 4. can do.
本実施形態の金属材の製造方法では、金属母材１ａ,１ｂの表面部位に供給した添加材１０を、回転ツール１００を用いた摩擦攪拌処理によって金属母材１ａ,１ｂ中に混入させる。金属母材１ａ,１ｂとしては、例えば、Ａｌ材、Ｆｅ材を適用することができる。 In the metal material manufacturing method of the present embodiment, the additive material 10 supplied to the surface portions of the metal base materials 1 a and 1 b is mixed into the metal base materials 1 a and 1 b by a friction stirring process using the rotary tool 100. As the metal base materials 1a and 1b, for example, an Al material or an Fe material can be applied.
本実施形態では、まず図２に示すように、金属母材１ａ,１ｂ同士を距離ｗに近接させるか幅ｗの溝を形成して攪拌部２０とし、攪拌部２０に添加材１０を充填する。ここで、回転ツール１００のプローブ１０２の径ｒに対して、ｒ≧２ｗとすることが攪拌部２０の状態を良好にするために好ましい。添加材１０は、金属母材１ａ,１ｂとの反応性を有する粉末状の金属あるいは非金属とし、例えば、Ａｌ、Ｃｕ、Ｆｅ、Ｃ、Ｍｇ等の粉状又は粒状の物質を適用することができる。添加材１０は、異なる複数種類の物質を含むものとでき、当該複数の物質の割合を変更することにより、攪拌部２０に形成される金属材の組成を変更することができる。加えて、攪拌部２０の凹部のギャップの幅ｗと回転ツール１００のプローブ径ｒとの比率を変化させることにより、攪拌部２０に流動する金属母材１ａ，１ｂの量を変動させることで攪拌部２０の組成を変化させることが可能となる。 In this embodiment, as shown in FIG. 2, first, as shown in FIG. 2, the metal base materials 1 a and 1 b are brought close to the distance w or a groove with a width w is formed to form the stirring unit 20, and the stirring unit 20 is filled with the additive 10. . Here, it is preferable that r ≧ 2w with respect to the diameter r of the probe 102 of the rotary tool 100 in order to improve the state of the stirring unit 20. The additive 10 is a powdered metal or non-metal having reactivity with the metal base materials 1a and 1b, and for example, a powdery or granular substance such as Al, Cu, Fe, C, or Mg can be applied. it can. The additive 10 can include a plurality of different types of substances, and the composition of the metal material formed in the stirring unit 20 can be changed by changing the ratio of the plurality of substances. In addition, by changing the ratio of the gap width w of the recess of the stirring unit 20 and the probe diameter r of the rotary tool 100, the amount of the metal base materials 1a and 1b flowing to the stirring unit 20 is changed to thereby perform stirring. The composition of the part 20 can be changed.
次に、図３に示すように、金属母材１ａ，１ｂの添加材１０を充填した攪拌部２０上に、回転ツール１００のプローブ１０２を当接させつつ回転させ、さらに攪拌部２０の長手方向に沿って回転ツール１００を移動させることにより、攪拌部２０に充填した添加材１０を回転ツール１００によって攪拌させ、添加材１０を金属母材１ａ，１ｂ中に混入させることができる。この場合、攪拌部２０の長手方向に沿って２回以上、回転ツール１００を通過させることが、攪拌部２０の状態を良好にするために好ましい。 Next, as shown in FIG. 3, the probe 102 of the rotary tool 100 is rotated while abutting the probe 102 of the rotary tool 100 on the stirring unit 20 filled with the additive 10 of the metal base materials 1 a and 1 b, and the longitudinal direction of the stirring unit 20 is further increased. By moving the rotary tool 100 along, the additive 10 filled in the stirring unit 20 can be agitated by the rotary tool 100, and the additive 10 can be mixed into the metal base materials 1a and 1b. In this case, it is preferable to pass the rotary tool 100 twice or more along the longitudinal direction of the stirring unit 20 in order to improve the state of the stirring unit 20.
また、図１に示すようなプローブ１０２を有する回転ツール１００により摩擦攪拌処理を行う前に、図１に示す回転ツール１００からプローブ１０２を除去した回転ツール１００の先端を、金属母材１ａ，１ｂの添加材１０を充填した攪拌部２０上に当接させつつ回転させ、さらに攪拌部２０の長手方向に沿って回転ツール１００を移動させることにより、粉状又は粒状の添加材１０を攪拌部２０に十分に押付けて圧縮し、プローブ１０２を有する回転ツール１００による摩擦攪拌処理の際に、攪拌部２０から添加材１０が漏れることを防止することができる。 Further, before the friction stir processing is performed by the rotary tool 100 having the probe 102 as shown in FIG. 1, the tip of the rotary tool 100 from which the probe 102 is removed from the rotary tool 100 shown in FIG. By rotating the rotating tool 100 along the longitudinal direction of the stirring unit 20, the powdery or granular additive 10 is mixed with the stirring unit 20 by rotating the rotating tool 100 along the longitudinal direction of the stirring unit 20. It is possible to prevent the additive 10 from leaking from the stirring unit 20 during the friction stirring process by the rotary tool 100 having the probe 102.
また、プローブ１０２を有する回転ツール１００による摩擦攪拌処理の際は、必ずしも、プローブ１０２を攪拌部２０の表面から深い部位まで挿入する必要はなく、攪拌部２０の浅い表層部において摩擦攪拌処理を行っても良い。なお、添加材を十分に混入させるため、回転ツール１００を、添加材１０を充填した攪拌部２０上で回転させつつ往復動させることもできる。 Further, when the friction stir processing is performed by the rotary tool 100 having the probe 102, it is not always necessary to insert the probe 102 from the surface of the stirrer 20 to a deep part, and the friction stir processing is performed on the shallow surface layer portion of the stirrer 20. May be. In order to sufficiently mix the additive, the rotary tool 100 can be reciprocated while rotating on the stirring unit 20 filled with the additive 10.
あるいは、回転ツール１００を移動させずに同じ場所で回転させ続けることによっても、添加材１０を金属母材１ａ，１ｂ中に混入させることができる。この場合、図４に示すように金属材１ａの表面から窪んだ攪拌部２０に添加材１０を充填し、図５に示すように回転ツール１００を金属母材１ａの同じ位置で回転させ続けることにより、スポット型の摩擦攪拌処理を行っても良い。この場合、添加材１０を連続した複数箇所で混入させることにより、金属母材１ａ，１ｂ上の広い領域で所望の金属材を製造することができる。 Alternatively, the additive 10 can be mixed into the metal base materials 1a and 1b by continuing to rotate the rotating tool 100 at the same place without moving. In this case, as shown in FIG. 4, the additive 10 is filled in the stirring unit 20 that is recessed from the surface of the metal material 1 a, and the rotating tool 100 is continuously rotated at the same position of the metal base material 1 a as shown in FIG. 5. Thus, a spot-type friction stirring process may be performed. In this case, a desired metal material can be manufactured in a wide area on the metal base materials 1a and 1b by mixing the additive material 10 at a plurality of continuous locations.
さらに、図６に示すように、板状の金属母材１ａ，１ｂを重ね合わせ、その間に添加材１０を充填して攪拌部２０とし、図７に示すように、回転ツール１００を金属母材１ａに当接させつつ回転させ、金属母材１ａ上を移動させることにより、攪拌部２０を攪拌する重ね合わせ接合に類似した態様で摩擦攪拌処理を行っても良い。この場合も、図８に示すように、回転ツール１００の移動を伴わないスポット型の摩擦攪拌処理とすることができる。 Further, as shown in FIG. 6, the plate-shaped metal base materials 1a and 1b are overlapped, and the additive material 10 is filled between them to form the stirring unit 20, and as shown in FIG. The friction stir processing may be performed in a manner similar to the superposition joining in which the stirrer 20 is stirred by rotating while abutting on the la and moving on the metal base material 1a. Also in this case, as shown in FIG. 8, a spot-type friction stirring process that does not involve the movement of the rotary tool 100 can be performed.
加えて、図２に示すような攪拌部２０に対しては、図９に示すように、複数の板状の添加材１０ａ，１０ｂを攪拌部２０に対して板面を垂直方向にして積層させて配置しても良い。あるいは、図１０に示すように、複数の板状の添加材１０ａ，１０ｂを攪拌部２０に対して板面を水平方向にして積層させて配置しても良い。添加材１０ａ，１０ｂの板厚及び数量を変更することにより、攪拌部２０に形成される金属材の組成を変更することができる。図６に示すような重ね合わせ接合に類似した手法においても、図１１に示すように、複数の板状の添加材１０ａ，１０ｂを攪拌部２０に対して板面を水平方向にして積層させて配置することができる。ただし、添加材１０を粉状又は粒状とした方が金属母材１ａ，１ｂとの界面が大きくなり、界面における化学反応が促進されるため、添加材１０を粉状又は粒状とした方が好適である。なお、添加材１０の粉又は粒の大きさは、一般に細かくすることにより、界面における化学反応が促進されるため望ましいが、添加材１０の粉又は粒が小さすぎると、例えば、添加材１０がＡｌ粉末の場合には、表面の酸化物により、不純物の混入に繋がるばかりか、金属母材１ａ，１ｂ同士の接合もやや困難になる場合がある。さらに、本実施形態における摩擦攪拌処理にあたり攪拌部２０に液体ＣＯ２や液体Ｎ２を用いることにより、冷却速度を増加させることも可能である。この場合には、後述するような好適な摩擦攪拌処理の条件範囲はより大きくなる。 In addition, for the stirring unit 20 as shown in FIG. 2, as shown in FIG. 9, a plurality of plate-like additives 10 a and 10 b are stacked with the plate surface perpendicular to the stirring unit 20. May be arranged. Alternatively, as shown in FIG. 10, a plurality of plate-like additive materials 10 a and 10 b may be disposed so as to be laminated with the plate surface horizontal with respect to the stirring unit 20. By changing the plate thickness and quantity of the additive materials 10a and 10b, the composition of the metal material formed in the stirring unit 20 can be changed. Also in the technique similar to the superposition joining as shown in FIG. 6, as shown in FIG. 11, a plurality of plate-like additive materials 10 a and 10 b are laminated with the plate surface in the horizontal direction with respect to the stirring unit 20. Can be arranged. However, if the additive 10 is powdery or granular, the interface with the metal base materials 1a and 1b becomes larger and the chemical reaction at the interface is promoted. Therefore, the additive 10 is preferably powdery or granular. It is. The size of the powder or particles of the additive 10 is generally desirable because the chemical reaction at the interface is promoted by making it fine, but if the powder or particles of the additive 10 are too small, for example, the additive 10 In the case of Al powder, the oxide on the surface not only leads to contamination of impurities, but also makes it difficult to join the metal base materials 1a and 1b. Moreover, by using liquid CO 2 or liquid N 2 to a stirred portion 20 Upon friction stir processing in the present embodiment, it is also possible to increase the cooling rate. In this case, the condition range of a suitable friction stirring process as described later becomes larger.
（実験例１：Ａｌ母材にＣｕを添加材として添加）
以下、異なる種類の金属母材１ａ，１ｂに対して異なる種類の添加材１０を攪拌部２０に攪拌させた実験例について説明する。金属母材１ａ，１ｂとして板状のＡ１０５０材を用意し、添加材１０として１００％の平均粒径１０６μｍのＣｕ粉末を用意した。図２に示すように、Ａ１０５０材の金属母材１ａ，１ｂの端部同士を２ｍｍの距離まで近接させて隙間を攪拌部２０とし、当該攪拌部２０に１００％のＣｕ粉末を充填した。図１に示すようなプローブ１０２のプローブ径６ｍｍ、プローブ長４．３ｍｍ、ショルダー１０１のショルダー径１５ｍｍの回転ツール１００を用意した。この回転ツール１００を図３に示すように攪拌部２０に当接させつつ回転させ、攪拌部２０に沿って移動させた。回転ツール１００の移動速度は１００ｍｍ／ｍｉｎ、回転速度は１５００ｒｐｍ、傾斜角は３°とした。
(Experimental example 1: Addition of Cu as additive to Al base material)
Hereinafter, experimental examples in which different types of additive 10 are stirred by the stirring unit 20 with respect to different types of metal base materials 1a and 1b will be described. A plate-shaped A1050 material was prepared as the metal base materials 1a and 1b, and a Cu powder having a 100% average particle size of 106 μm was prepared as the additive material 10. As shown in FIG. 2, the end portions of the metal base materials 1a and 1b of the A1050 material were brought close to a distance of 2 mm to form a gap as the stirring unit 20, and the stirring unit 20 was filled with 100% Cu powder. A rotating tool 100 having a probe diameter of 6 mm, a probe length of 4.3 mm, and a shoulder 101 of 15 mm as shown in FIG. 1 was prepared. As shown in FIG. 3, the rotating tool 100 was rotated while being in contact with the stirring unit 20, and moved along the stirring unit 20. The moving speed of the rotating tool 100 was 100 mm / min, the rotating speed was 1500 rpm, and the inclination angle was 3 °.
図１２に示すように、攪拌部２０付近は、回転ツール１００の１パス（通過）後は攪拌部２０の硬さが向上していることが判る。さらに、攪拌部２０付近は、回転ツールの２パス後は攪拌部２０における硬度の分布がより均一となっていることが判る。金属母材１ａ，１ｂの硬さは４０．３Ｈｖであるのに対し攪拌部では最大８２．５Ｈｖの硬さを示したことから、Ｃｕ粉末を攪拌部２０に添加することにより、硬度が金属母材１ａ，１ｂの２倍以上となることが判る。 As shown in FIG. 12, it can be seen that in the vicinity of the stirring unit 20, the hardness of the stirring unit 20 is improved after one pass (pass) of the rotary tool 100. Furthermore, it can be seen that the hardness distribution in the stirring unit 20 is more uniform in the vicinity of the stirring unit 20 after two passes of the rotary tool. The hardness of the metal base materials 1a and 1b was 40.3Hv, whereas the stirrer exhibited a maximum hardness of 82.5Hv. Therefore, by adding Cu powder to the stirrer 20, the hardness was increased to the metal base. It turns out that it becomes 2 times or more of material 1a, 1b.
１パス後の攪拌部２０のＳＥＭ写真である図１３、及び２パス後の攪拌部２０のＳＥＭ写真である図１４に示すように、すべての観察点で均一なＣｕ粒子の分散が観察され、出発原料のＣｕ粉末よりも粒径が小さくなっていることが確認された。このことより、摩擦攪拌処理が添加材１０の微細化と均一分散に効果的であることが判る。しかしながら、Ａｌ中のＣｕ粒子は１パス後もほぼ均一に分散しており、Ｃｕ粒子の均一分散という点だけでは２パス後の攪拌部２０の硬度が均一に向上したことは説明できない。図１３に示すように、このとき、ＨＡＺ部（熱影響部）での軟化が観察されるが、回転ツール１００の移動速度を大きくしたり、下院店ツール１００の回転速度を小さくすることで、これを抑制することができる。 As shown in FIG. 13 which is an SEM photograph of the stirring unit 20 after one pass and FIG. 14 which is an SEM photograph of the stirring unit 20 after two passes, uniform dispersion of Cu particles is observed at all observation points. It was confirmed that the particle size was smaller than the starting Cu powder. From this, it can be seen that the friction stirring treatment is effective for the refinement and uniform dispersion of the additive 10. However, Cu particles in Al are almost uniformly dispersed after one pass, and it cannot be explained that the hardness of the stirring unit 20 after two passes is uniformly improved only by the uniform dispersion of Cu particles. As shown in FIG. 13, at this time, softening in the HAZ part (heat affected part) is observed, but by increasing the moving speed of the rotating tool 100 or decreasing the rotating speed of the lower house tool 100, This can be suppressed.
２パス後の攪拌部２０のＴＥＭ写真である図１５に示すように、２プロセス後のＴＥＭ像より、白色のＡｌマトリクス中に、ナノスケールの黒色の粒子が観察され、ＳＡＤパターンの結果、この粒子はＡｌ２Ｃｕの組成をもつ金属間化合物であることが確認された。すなわち、本実施形態では、摩擦攪拌接合という１つの接合法を利用して、Ａｌの金属母材１ａ，１ｂ中にＣｕ粒子の分散、拡散、析出といった３つの過程を実現することができる。なお、図１６に示すように、Ａｌの金属母材１ａ，１ｂ中には、ＡｌＣｕの形でも結晶が析出していることが判る。 As shown in FIG. 15 which is a TEM photograph of the stirring unit 20 after two passes, nanoscale black particles are observed in the white Al matrix from the TEM image after the two processes. As a result of the SAD pattern, The particles were confirmed to be intermetallic compounds having a composition of Al 2 Cu. That is, in the present embodiment, three processes such as dispersion, diffusion and precipitation of Cu particles in the Al metal base materials 1a and 1b can be realized by using one joining method called friction stir welding. As shown in FIG. 16, it can be seen that crystals are precipitated in the form of AlCu in the Al metal base materials 1a and 1b.
Ａｌの金属母材１ａ，１ｂ中のＣｕ粒子のＳＥＭ写真である図１７、及び当該Ｃｕ粒子の組成を示す図１８にあるように、Ａｌの金属母材１ａ，１ｂ中のＣｕ粒子はＡｌ中で反応し、Ｃｕ粒子の周辺の位置Ｐ１からＣｕ粒子の中心の位置Ｐ４に至るにつれて、Ａｌに対するＣｕの割合が増加していることが判る。図１７に示すように、Ｃｕ粒子中に異なる組成のいくつかの反応相の生成が観察された。図１８は各反応層のＥＤＳ分析の結果を示す。２番の層である位置Ｐ２ではアルミニウムと銅が３対１の割合で、３番の層である位置Ｐ３では９対１１の割合で存在しており、Ｃｕ粒子中にはＡｌ−ｒｉｃｈ相とＣｕ−ｒｉｃｈ相が形成されていることが確認された。すべての粒子で同様に反応相が形成されていることが示唆され、添加材１０としてＣｕ粉末を用いたことが、ＡｌとＣｕの反応界面積を増加させ、Ａｌマトリクス中への反応生成物の分散能を向上させたと考えられる。 As shown in FIG. 17 which is an SEM photograph of Cu particles in the Al metal base materials 1a and 1b and FIG. 18 which shows the composition of the Cu particles, the Cu particles in the Al metal base materials 1a and 1b are in Al. It can be seen that the ratio of Cu to Al increases from the position P1 around the Cu particles to the position P4 at the center of the Cu particles. As shown in FIG. 17, the formation of several reaction phases with different compositions in the Cu particles was observed. FIG. 18 shows the results of EDS analysis of each reaction layer. In position P2, which is the second layer, aluminum and copper are present in a ratio of 3: 1, and in position P3, which is the third layer, there is a ratio of 9:11. In the Cu particles, Al-rich phase and It was confirmed that a Cu-rich phase was formed. It is suggested that the reaction phase is similarly formed in all the particles, and the use of Cu powder as the additive 10 increases the reaction interfacial area of Al and Cu, and the reaction product into the Al matrix. It is thought that the dispersibility was improved.
金属母材１ａ，１ｂ同士の隙間（ギャップ幅）を２ｍｍ、３ｍｍ、４ｍｍと変化させ、回転ツール１００のパス数を変化させて、上記と同様に攪拌部２０にＣｕの添加材１０を攪拌させた。図１９に丸印で示すように、示すように、プローブ径６ｍｍに対して、２分の１以下のギャップ幅３ｍｍでは、２パス後に良好な攪拌部２０が得られていることが判る。なお３プロセス後も、図１６と同様のナノスケールの黒色の粒子が観察され、ＳＡＤパターンの結果この粒子はＡｌＣｕの組成をもつ金属間化合物であることが確認された。粒子の粒径は２００ｎｍ程度であることから均一な硬さの増加はナノオーダーの金属間化合物がＡｌマトリックス中に均一に分布したためであると考えられる。これは、摩擦攪拌処理による強ひずみとその過程で生じる熱が金属間化合物生成に寄与したと考えられる。 The gap (gap width) between the metal base materials 1a and 1b is changed to 2 mm, 3 mm, and 4 mm, and the number of passes of the rotary tool 100 is changed, and the Cu additive 10 is stirred in the stirring unit 20 in the same manner as described above. It was. As indicated by a circle in FIG. 19, it can be seen that a good stirring portion 20 is obtained after two passes when the gap width is 3 mm or less with respect to the probe diameter of 6 mm. Note that nanoscale black particles similar to those in FIG. 16 were observed after three processes. As a result of the SAD pattern, it was confirmed that these particles were an intermetallic compound having an AlCu composition. Since the particle size of the particles is about 200 nm, the uniform increase in hardness is considered to be due to the fact that nano-order intermetallic compounds are uniformly distributed in the Al matrix. This is thought to be due to the strong strain caused by the friction stir treatment and the heat generated in the process contributing to the formation of intermetallic compounds.
金属母材１ａ，１ｂ同士のギャップ幅を２ｍｍとし、１００％のＣｕ粉末、混合比が３：７のＣｕ粉末とＡｌ粉末との混合粉末を添加材１０として、回転ツール１００のパス数を変化させて、上記と同様に攪拌部２０にＣｕの添加材１０を攪拌させた。なお、Ａｌ粉末の平均粒径は８９μｍであった。図２０の表及び図２１〜２３のグラフに示す３０％のＣｕ粉末を攪拌させた攪拌部２０付近の硬度分布より、ＣｕとＡｌとの混合粉末を添加材１０として用いても、攪拌部２０付近の硬度を向上させることができることが判る。この場合においても、２パス以上の加工を加えることにより、攪拌部２０付近の硬度分布がより均一になることが判る。 The gap width between the metal base materials 1a and 1b is set to 2 mm, and the number of passes of the rotary tool 100 is changed by using 100% Cu powder and a mixed powder of Cu powder and Al powder with a mixing ratio of 3: 7 as additive 10. In the same manner as described above, the Cu additive 10 was stirred in the stirring unit 20. The average particle size of the Al powder was 89 μm. From the hardness distribution in the vicinity of the stirring unit 20 in which 30% of the Cu powder shown in the table of FIG. 20 and the graphs of FIGS. 21 to 23 is stirred, even if a mixed powder of Cu and Al is used as the additive 10, the stirring unit 20 It can be seen that the hardness in the vicinity can be improved. Also in this case, it can be seen that the hardness distribution near the stirring unit 20 becomes more uniform by applying processing of two passes or more.
（実験例２：Ａｌ母材にＳｉＣを添加材として添加）
Ａｌの金属母材１ａ，１ｂとの反応性はないが、参考のため、混合比が１：９のＣｕ粉末とＳｉＣ粉末との混合粉末を添加材１０として、回転ツール１００のパス数を変化させて、上記と同様に攪拌部２０にＳｉＣの添加材１０を攪拌させた。図２４〜２６のグラフに示すＳｉＣ粉末を攪拌させた攪拌部２０付近の硬度分布より、ＳｉＣ粉末を攪拌部２０に攪拌することで、攪拌部２０付近と周辺のＡｌの金属母材１ａ，１ｂとで硬度分布を均一にすることができることが判る。これにより、例えば、金属母材１ａ，１ｂ同士を接合する際に、ＳｉＣ粉末を接合部となる攪拌部２０に添加材１０として充填することにより、接合部である攪拌部２０の硬度を周囲と均一に保つことが可能となる。
(Experimental example 2: SiC is added to the Al base material as an additive)
Although there is no reactivity with the Al metal base materials 1a and 1b, the number of passes of the rotary tool 100 is changed using a mixed powder of Cu powder and SiC powder with a mixing ratio of 1: 9 as an additive 10 for reference. In the same manner as described above, the SiC additive 10 was stirred in the stirring unit 20. From the hardness distribution in the vicinity of the stirring unit 20 in which the SiC powder shown in the graphs of FIGS. 24 to 26 is stirred, by stirring the SiC powder in the stirring unit 20, the Al metal bases 1a and 1b in the vicinity of the stirring unit 20 and the surrounding area are obtained. It can be seen that the hardness distribution can be made uniform. Thereby, for example, when joining the metal base materials 1a and 1b, the stirrer 20 serving as the joint is filled with the SiC powder with the stirrer 20 serving as the joint as the additive 10 so that the hardness of the stirrer 20 serving as the joint is around. It becomes possible to keep it uniform.
（実験例３：Ａｌ母材にＦｅを添加材として添加）
金属母材１ａ，１ｂ同士のギャップ幅を２ｍｍとし、１００％のＦｅ粉末、を添加材１０として、回転ツール１００のパス数を変化させて、上記と同様に攪拌部２０にＦｅの添加材１０を攪拌させた。図２７〜２９のグラフに示すＦｅ粉末を攪拌させた攪拌部２０付近のの硬度分布より、１００％のＦｅ粉末を添加材１０として用いても、攪拌部２０付近の硬度を向上させることができることが判る。この場合においても、２パス以上の加工を加えることにより、攪拌部２０付近の硬度分布がより均一になることが判る。なお、１００％のＦｅ粉末を添加材１０として用いた場合に、１００％のＣｕ粉末を添加材１０として用いた場合に比べて攪拌部２０周辺の硬度の上昇が低いのは、図３０のＡｌとＣｕの状態図、及び図３１のＡｌとＦｅの状態図に示すように、Ｃｕに比べてＦｅの固溶度が低いためと考えられる。すなわち、Ｃｕの場合は摩擦攪拌処理中にＡｌ中に固溶し、冷却中に析出してＡｌ２Ｃｕとなるため、硬度が強くなる。一方、Ｆｅの場合は摩擦攪拌処理中に固溶しないため、Ａｌ中に小さく分散し、Ｆｅ粒子と、Ｆｅ粒子の界面に生成する金属間化合物とによりある程度は硬度が向上するが、Ｃｕのように析出はしないため、上記のような結果になると考えれる。
(Experimental example 3: Fe added to Al base material as additive)
The gap width between the metal base materials 1a and 1b is 2 mm, 100% Fe powder is used as the additive 10, and the number of passes of the rotary tool 100 is changed. Was allowed to stir. From the hardness distribution in the vicinity of the stirring unit 20 in which the Fe powder shown in the graphs of FIGS. 27 to 29 is stirred, even if 100% Fe powder is used as the additive 10, the hardness in the vicinity of the stirring unit 20 can be improved. I understand. Also in this case, it can be seen that the hardness distribution near the stirring unit 20 becomes more uniform by applying processing of two passes or more. Note that when 100% Fe powder is used as additive 10, the increase in hardness around stirring unit 20 is lower than when 100% Cu powder is used as additive 10. As shown in the phase diagram of Cu and Cu and the phase diagram of Al and Fe in FIG. 31, it is considered that the solid solubility of Fe is lower than that of Cu. That is, in the case of Cu, since it dissolves in Al during the friction stir processing and precipitates during cooling to become Al 2 Cu, the hardness increases. On the other hand, in the case of Fe, since it does not form a solid solution during the friction stir processing, it is dispersed in a small amount in Al, and the hardness is improved to some extent by the Fe particles and the intermetallic compound produced at the interface between the Fe particles. It is considered that the above results are obtained because no precipitation occurs.
（実験例４：Ｆｅ母材にＣを添加材として添加）
金属母材１ａ，１ｂとして板状のパーライト系鋳鉄を用意し、添加材１０として１００％の黒鉛粉末を用意した。回転ツールとしては、図１に示す回転ツールからプローブ１０２を除去したものを用意した。ショルダー径は２５ｍｍとした。金属母材１ａ，１ｂ同士のギャップ幅を２ｍｍとし、回転ツール１００の移動速度及び回転速度を変更しつつ、上記と同様に攪拌部２０に黒鉛の添加材１０を攪拌させた。また、添加材１０を添加しないパーライト系鋳鉄についても、摩擦攪拌処理による表面焼入れの効果を検証するため、同様に回転ツールにより表面を攪拌した。
(Experimental example 4: C added to Fe base material as additive)
Plate-like pearlite cast iron was prepared as the metal base materials 1 a and 1 b, and 100% graphite powder was prepared as the additive 10. As the rotating tool, a tool obtained by removing the probe 102 from the rotating tool shown in FIG. 1 was prepared. The shoulder diameter was 25 mm. While the gap width between the metal base materials 1a and 1b was set to 2 mm and the moving speed and the rotating speed of the rotary tool 100 were changed, the stirring material 20 was stirred in the stirring part 20 in the same manner as described above. Further, the surface of pearlite cast iron to which the additive 10 was not added was similarly stirred with a rotating tool in order to verify the effect of surface quenching by the friction stirring process.
ここで、攪拌部２０に対する入熱Ｔには、Ｔ∝（回転ツールの回転速度×回転ツールの攪拌部への荷重）／回転ツール移動速度、あるいはＴ∝（回転ツールの回転速度×回転ツールの攪拌部への荷重×回転ツールのショルダー径）／回転ツール移動速度の関係が成り立つ。 Here, the heat input T to the stirring unit 20 includes T に は (rotation speed of the rotary tool × load to the stirring unit of the rotary tool) / rotation tool moving speed, or T∝ (rotation speed of the rotary tool × rotation tool). The relationship of the load on the stirring portion × the shoulder diameter of the rotary tool) / the rotational speed of the rotary tool is established.
ここで図３２に示すように、黒鉛粉末の添加材１０を添加しないパーライト系鋳鉄よりも、黒鉛粉末の添加材１０を添加した攪拌部２０を良好な状態とする回転ツールの回転速度、荷重及び移動速度の適正な範囲は、Ｆｅ中へのＣの拡散が必要なため、狭くなる。この場合、３０００００００［ｒ・ｋｇ／ｍ］≦（回転ツールの回転速度［ｒｐｍ］×回転ツールの攪拌部への荷重［ｋｇ］）／回転ツール移動速度［ｍ／ｍｉｎ］＜１５０００００００［ｒ・ｋｇ／ｍ］、あるいは、７５００００［ｒ・ｋｇ］≦（回転ツールの回転速度［ｒｐｍ］×回転ツールの攪拌部への荷重［ｋｇ］×回転ツールのショルダー径［ｍ］）／回転ツール移動速度［ｍ／ｍｉｎ］＜３７５００００［ｒ・ｋｇ］を満たすように、攪拌を行なうことが攪拌部２０を良好な状態とするために好ましい。図３３に示した実験結果により、上記条件を満たすことにより、良好な攪拌部２０を得ることができることが判る。 Here, as shown in FIG. 32, the rotational speed, load, and load of the rotating tool that makes the stirring unit 20 to which the graphite powder additive 10 is added better than the pearlite cast iron to which the graphite powder additive 10 is not added. The appropriate range of the moving speed becomes narrow because C needs to diffuse into Fe. In this case, 30000000 [r · kg / m] ≦ (rotational tool rotational speed [rpm] × rotary tool stirring portion load [kg]) / rotary tool moving speed [m / min] <150000000 [r · kg] / M] or 750000 [r · kg] ≦ (rotational tool rotational speed [rpm] × rotary tool stirring portion [kg] × rotary tool shoulder diameter [m]) / rotary tool moving speed [ m / min] <3750000 [r · kg] is preferably performed so that the stirring unit 20 is in a good state. It can be seen from the experimental results shown in FIG. 33 that a satisfactory stirring unit 20 can be obtained by satisfying the above conditions.
また、上記の２式は、金属母材１ａ，１ｂとして、厚さ５ｍｍ、幅１００ｍｍ、長さ３００ｍｍの板状の試料を用いた場合に対するものである。したがって、より厚さが厚い金属母材１ａ，１ｂに関しては、上限の値をそれぞれ金属母材１ａ，１ｂの板厚ｔ［ｍｍ］に対して１５０００００００×ｔ／５、及び３７５００００×ｔ／５とするのが望ましい。一方、より厚さが薄い金属母材１ａ，１ｂに関しては、下限である値をそれぞれ金属母材１ａ，１ｂの板厚ｔ［ｍｍ］に対して３０００００００×ｔ／５及び７５００００×ｔ／５とするのが望ましい。 The above two formulas are for the case where a plate-like sample having a thickness of 5 mm, a width of 100 mm, and a length of 300 mm is used as the metal base materials 1a and 1b. Therefore, with respect to the thicker metal base materials 1a and 1b, the upper limit values are 150000000 × t / 5 and 3750000 × t / 5 with respect to the plate thickness t [mm] of the metal base materials 1a and 1b, respectively. It is desirable to do. On the other hand, for the metal base materials 1a and 1b having a smaller thickness, the lower limit values are 30000000 × t / 5 and 750000 × t / 5 with respect to the plate thickness t [mm] of the metal base materials 1a and 1b, respectively. It is desirable to do.
この場合、上記の２式は、５ｍｍより厚さが厚い金属母材１ａ，１ｂに関しては、３０００００００［ｒ・ｋｇ／ｍ］≦（回転ツールの回転速度［ｒｐｍ］×回転ツールの攪拌部への荷重［ｋｇ］）／回転ツール移動速度［ｍ／ｍｉｎ］＜１５０００００００×ｔ／５［ｒ・ｋｇ／ｍ］、及び７５００００［ｒ・ｋｇ］＜（回転ツールの回転速度［ｒｐｍ］×回転ツールの攪拌部への荷重［ｋｇ］×回転ツールのショルダー径［ｍ］）／回転ツール移動速度［ｍ／ｍｉｎ］≦３７５００００［ｒ・ｋｇ］×ｔ／５となる。 In this case, the above two formulas are 30000000 [r · kg / m] ≦ (rotational speed of the rotary tool [rpm] × rotation tool to the stirring unit for the metal base materials 1a and 1b having a thickness greater than 5 mm. Load [kg]) / rotating tool moving speed [m / min] <150000000 × t / 5 [r · kg / m], and 750,000 [r · kg] <(rotating tool rotating speed [rpm] × rotating tool The load to the stirrer [kg] × the shoulder diameter of the rotating tool [m]) / the rotating tool moving speed [m / min] ≦ 3750000 [r · kg] × t / 5.
一方、上記の２式は、５ｍｍより厚さが薄い金属母材１ａ，１ｂに関しては、３０００００００×ｔ／５［ｒ・ｋｇ／ｍ］≦（回転ツールの回転速度［ｒｐｍ］×回転ツールの攪拌部への荷重［ｋｇ］）／回転ツール移動速度［ｍ／ｍｉｎ］＜１５０００００００［ｒ・ｋｇ／ｍ］、及び７５００００×ｔ／５［ｒ・ｋｇ］≦（回転ツールの回転速度［ｒｐｍ］×回転ツールの攪拌部への荷重［ｋｇ］×回転ツールのショルダー径［ｍ］）／回転ツール移動速度［ｍ／ｍｉｎ］＜３７５００００［ｒ・ｋｇ］となる。 On the other hand, in the above two formulas, 30000000 × t / 5 [r · kg / m] ≦ (rotational speed [rpm] × rotating tool agitation) for the metal base materials 1a and 1b having a thickness of less than 5 mm. Load [kg]) / rotating tool moving speed [m / min] <150000000 [r · kg / m], and 750,000 × t / 5 [r · kg] ≦ (rotating tool rotating speed [rpm] × The load on the stirring part of the rotary tool [kg] × the shoulder diameter of the rotary tool [m]) / the rotational tool moving speed [m / min] <3750000 [r · kg].
さらに、上記４式は回転ツール１００の前進角を３°とした場合に対するものであり、前進角θ［°］をこれより大きくした場合には、接触面積が小さくなりより局所的に加熱されるため、温度が上昇し、前進角θ［°］を小さくした場合には、温度が低下することが予測される。したがって、回転ツール１００の前進角θ［°］が３°以上の場合には、上記２式の下限の値を３０００００００×ｃｏｓθ／ｃｏｓ（３°）、及び７５００００×ｃｏｓθ／ｃｏｓ（３°）とすることが望ましい。 Further, the above four formulas are for the case where the advancing angle of the rotary tool 100 is 3 °, and when the advancing angle θ [°] is made larger than this, the contact area becomes smaller and it is heated more locally. Therefore, when the temperature rises and the advance angle θ [°] is reduced, it is predicted that the temperature will fall. Therefore, when the advance angle θ [°] of the rotary tool 100 is 3 ° or more, the lower limit values of the above two formulas are 30000000 × cos θ / cos (3 °) and 750000 × cos θ / cos (3 °). It is desirable to do.
この場合、上記４式は、３０００００００×ｃｏｓθ／ｃｏｓ（３°）［ｒ・ｋｇ／ｍ］≦（回転ツールの回転速度［ｒｐｍ］×回転ツールの攪拌部への荷重［ｋｇ］）／回転ツール移動速度［ｍ／ｍｉｎ］＜１５０００００００［ｒ・ｋｇ／ｍ］、７５００００×ｃｏｓθ／ｃｏｓ（３°）［ｒ・ｋｇ］≦（回転ツールの回転速度［ｒｐｍ］×回転ツールの攪拌部への荷重［ｋｇ］×回転ツールのショルダー径［ｍ］）／回転ツール移動速度［ｍ／ｍｉｎ］＜３７５００００［ｒ・ｋｇ］、５ｍｍより厚さが厚い金属母材１ａ，１ｂに関しては、３０００００００×ｃｏｓθ／ｃｏｓ（３°）［ｒ・ｋｇ／ｍ］≦（回転ツールの回転速度［ｒｐｍ］×回転ツールの攪拌部への荷重［ｋｇ］）／回転ツール移動速度［ｍ／ｍｉｎ］＜１５０００００００×ｔ／５［ｒ・ｋｇ／ｍ］、及び７５００００×ｃｏｓθ／ｃｏｓ（３°）［ｒ・ｋｇ］≦（回転ツールの回転速度［ｒｐｍ］×回転ツールの攪拌部への荷重［ｋｇ］×回転ツールのショルダー径［ｍ］）／回転ツール移動速度［ｍ／ｍｉｎ］＜３７５００００×ｔ／５［ｒ・ｋｇ］となり、５ｍｍより厚さが薄い金属母材１ａ，１ｂに関しては、３０００００００×ｔ／５×ｃｏｓθ／ｃｏｓ（３°）［ｒ・ｋｇ／ｍ］≦（回転ツールの回転速度［ｒｐｍ］×回転ツールの攪拌部への荷重［ｋｇ］）／回転ツール移動速度［ｍ／ｍｉｎ］＜１５０００００００［ｒ・ｋｇ／ｍ］、及び７５００００×ｔ／５×ｃｏｓθ／ｃｏｓ（３°）［ｒ・ｋｇ］≦（回転ツールの回転速度［ｒｐｍ］×回転ツールの攪拌部への荷重［ｋｇ］×回転ツールのショルダー径［ｍ］）／回転ツール移動速度［ｍ／ｍｉｎ］＜３７５００００［ｒ・ｋｇ］となる。 In this case, the above four formulas are: 30000000 × cos θ / cos (3 °) [r · kg / m] ≦ (rotational tool rotation speed [rpm] × rotary tool stirring portion load [kg]) / rotary tool Moving speed [m / min] <150000000 [r · kg / m], 750000 × cos θ / cos (3 °) [r · kg] ≦ (Rotating tool rotating speed [rpm] × Rotating tool load on stirring unit [Kg] × shoulder diameter of rotating tool [m]) / rotating tool moving speed [m / min] <3750000 [r · kg] For metal base materials 1a and 1b thicker than 5 mm, 30000000 × cos θ / cos (3 °) [r · kg / m] ≦ (rotational tool rotational speed [rpm] × rotary tool stirring portion load [kg]) / rotary tool moving speed [m / min] <15000000 × t / 5 [r · kg / m] and 750000 × cos θ / cos (3 °) [r · kg] ≦ (Rotational speed of rotating tool [rpm] × Load on stirring portion of rotating tool [kg] × Rotating tool shoulder diameter [m]) / rotating tool moving speed [m / min] <3750000 × t / 5 [r · kg], and for metal base materials 1a and 1b having a thickness of less than 5 mm, 30000000 × t / 5 × cos θ / cos (3 °) [r · kg / m] ≦ (rotational tool rotation speed [rpm] × rotary tool stirring portion load [kg]) / rotary tool moving speed [m / min] <150000000 [r · kg / m] and 750000 × t / 5 × cos θ / cos (3 °) [r · kg] ≦ (rotational tool rotation speed [rpm] × rotational tool load on stirring unit [kg ] X Rotating tool shoulder Diameter [m]) / Rotary tool moving speed [m / min] <3750000 [r · kg].
また、前進角θ［°］が３°以下の場合には、上記４式の上限の値を１５０００００００×ｃｏｓθ／ｃｏｓ（３°）、３７５００００×ｃｏｓθ／ｃｏｓ（３°）、１５０００００００××ｔ／５×ｃｏｓθ／ｃｏｓ（３°）、及び３７５００００［ｒ・ｋｇ］×ｔ／５ｃｏｓθ／ｃｏｓ（３°）とすることが望ましい。 When the advance angle θ [°] is 3 ° or less, the upper limit values of the above four expressions are 150000000 × cos θ / cos (3 °), 3750000 × cos θ / cos (3 °), 150000000 ×× t / 5 × cos θ / cos (3 °) and 3750000 [r · kg] × t / 5 cos θ / cos (3 °) are desirable.
この場合、上記４式は、３０００００００×［ｒ・ｋｇ／ｍ］≦（回転ツールの回転速度［ｒｐｍ］×回転ツールの攪拌部への荷重［ｋｇ］）／回転ツール移動速度［ｍ／ｍｉｎ］＜１５０００００００×ｃｏｓθ／ｃｏｓ（３°）［ｒ・ｋｇ／ｍ］、７５００００×［ｒ・ｋｇ］≦（回転ツールの回転速度［ｒｐｍ］×回転ツールの攪拌部への荷重［ｋｇ］×回転ツールのショルダー径［ｍ］）／回転ツール移動速度［ｍ／ｍｉｎ］＜３７５００００×ｃｏｓθ／ｃｏｓ（３°）［ｒ・ｋｇ］、５ｍｍより厚さが厚い金属母材１ａ，１ｂに関しては、３０００００００［ｒ・ｋｇ／ｍ］≦（回転ツールの回転速度［ｒｐｍ］×回転ツールの攪拌部への荷重［ｋｇ］）／回転ツール移動速度［ｍ／ｍｉｎ］＜１５０００００００×ｔ／５×ｃｏｓθ／ｃｏｓ（３°）［ｒ・ｋｇ／ｍ］、及び７５００００［ｒ・ｋｇ］≦（回転ツールの回転速度［ｒｐｍ］×回転ツールの攪拌部への荷重［ｋｇ］×回転ツールのショルダー径［ｍ］）／回転ツール移動速度［ｍ／ｍｉｎ］＜３７５００００×ｔ／５×ｃｏｓθ／ｃｏｓ（３°）［ｒ・ｋｇ］となり、５ｍｍより厚さが薄い金属母材１ａ，１ｂに関しては、３０００００００×ｔ／５［ｒ・ｋｇ／ｍ］≦（回転ツールの回転速度［ｒｐｍ］×回転ツールの攪拌部への荷重［ｋｇ］）／回転ツール移動速度［ｍ／ｍｉｎ］＜１５０００００００×ｃｏｓθ／ｃｏｓ（３°）［ｒ・ｋｇ／ｍ］、及び７５００００×ｔ／５［ｒ・ｋｇ］≦（回転ツールの回転速度［ｒｐｍ］×回転ツールの攪拌部への荷重［ｋｇ］×回転ツールのショルダー径［ｍ］）／回転ツール移動速度［ｍ／ｍｉｎ］＜３７５００００×ｃｏｓθ／ｃｏｓ（３°）［ｒ・ｋｇ］となり In this case, the above four formulas are 30000000 × [r · kg / m] ≦ (rotational tool rotation speed [rpm] × rotary tool stirring portion load [kg]) / rotary tool moving speed [m / min]. <150000000 × cos θ / cos (3 °) [r · kg / m], 750000 × [r · kg] ≦ (rotational tool rotation speed [rpm] × rotational tool load [kg] × rotary tool Shoulder diameter [m]) / rotary tool moving speed [m / min] <3750000 × cos θ / cos (3 °) [r · kg] For metal base materials 1a and 1b thicker than 5 mm, 30000000 [ r · kg / m] ≦ (rotational tool rotation speed [rpm] × rotary tool stirring portion load [kg]) / rotary tool moving speed [m / min] <150000000 × t / 5 × cos θ / c s (3 °) [r · kg / m] and 750000 [r · kg] ≦ (rotational tool rotation speed [rpm] × rotary tool stirring portion load [kg] × rotary tool shoulder diameter [m ] / Rotary tool moving speed [m / min] <3750000 × t / 5 × cos θ / cos (3 °) [r · kg], and for the metal base materials 1a and 1b having a thickness of less than 5 mm, 30000000 × t / 5 [r · kg / m] ≦ (rotational tool rotational speed [rpm] × rotary tool stirring portion load [kg]) / rotary tool moving speed [m / min] <150000000 × cos θ / cos ( 3 °) [r · kg / m], and 750,000 × t / 5 [r · kg] ≦ (rotational tool rotation speed [rpm] × rotary tool stirring portion load [kg] × rotary tool shoulder diameter [M]) / Rotation toe Moving speed [m / min] <3750000 × cosθ / cos (3 °) [r · kg] becomes
なお、上記条件は特に１回目の回転ツール１００の攪拌部２０への通過の際に満たすことが好ましい。しかし、２回目の回転ツール１００の攪拌部２０への通過の際には、１回目の通過で攪拌部２０が十分に攪拌されているため、攪拌部２０の冷却速度の方が重要となる。攪拌部２０の冷却速度は回転ツール１００の移動速度に関連するため、２回目以降の回転ツール１００の攪拌部２０への通過の際には、上記条件には限らず、回転ツール１００の移動速度は、０．６［ｍ／ｍｉｎ］以上、４［ｍ／ｍｉｎ］以下として攪拌を行なうことで、攪拌部２０を、回転ツール１００を１回のみ通過させるときよりも、さらに良好な状態とすることができる。つまり、１パス目が、３０００００００［ｒ・ｋｇ／ｍ］≦（回転ツールの回転速度［ｒｐｍ］×回転ツールの攪拌部への荷重［ｋｇ］）／回転ツール移動速度［ｍ／ｍｉｎ］とし、２パス目が、１５０００００［ｒ・ｋｇ／ｍ］≦（回転ツールの回転速度［ｒｐｍ］×回転ツールの攪拌部への荷重［ｋｇ］）／回転ツール移動速度［ｍ／ｍｉｎ］＜１５０００００００［ｒ・ｋｇ／ｍ］とすることが好適である。 In addition, it is preferable to satisfy | fill the said conditions at the time of passage to the stirring part 20 of the rotating tool 100 for the 1st time especially. However, when the second rotating tool 100 passes through the stirring unit 20, the cooling rate of the stirring unit 20 is more important because the stirring unit 20 is sufficiently stirred by the first pass. Since the cooling speed of the stirring unit 20 is related to the moving speed of the rotary tool 100, the second and subsequent passes of the rotating tool 100 to the stirring unit 20 are not limited to the above conditions, and the moving speed of the rotary tool 100 Is 0.6 [m / min] or more and 4 [m / min] or less to perform stirring so that the stirring unit 20 is in a better state than when the rotating tool 100 is passed only once. be able to. That is, the first pass is 30000000 [r · kg / m] ≦ (rotational tool rotation speed [rpm] × rotary tool stirring portion load [kg]) / rotary tool moving speed [m / min], The second pass is 1500,000 [r · kg / m] ≦ (rotational tool rotational speed [rpm] × rotary tool stirring section load [kg]) / rotary tool moving speed [m / min] <150000000 [r -Kg / m] is preferable.
あるいは、１パス目が、７５００００［ｒ・ｋｇ］＜（回転ツールの回転速度［ｒｐｍ］×回転ツールの攪拌部への荷重［ｋｇ］×回転ツールのショルダー径［ｍ］）／回転ツール移動速度［ｍ／ｍｉｎ］とし、２パス目が、３７５００［ｒ・ｋｇ］≦（回転ツールの回転速度［ｒｐｍ］×回転ツールの攪拌部への荷重［ｋｇ］×回転ツールのショルダー径［ｍ］）／回転ツール移動速度［ｍ／ｍｉｎ］＜３７５００００［ｒ・ｋｇ］ Alternatively, the first pass is 750,000 [r · kg] <(rotational tool rotational speed [rpm] × rotary tool stirring portion [kg] × rotary tool shoulder diameter [m]) / rotary tool moving speed. [M / min], the second pass is 37500 [r · kg] ≦ (rotational tool rotation speed [rpm] × rotary tool stirring portion load [kg] × rotary tool shoulder diameter [m]) / Rotary tool moving speed [m / min] <3750000 [r · kg]
なお、以下、他の金属母材１ａ，１ｂ及び添加材２０の組合せについて述べる。 Hereinafter, combinations of other metal base materials 1a and 1b and additive 20 will be described.
（Ａｌを金属母材とした他の添加材の組合せ）
上述したＡｌの金属母材１ａ，１ｂにＣｕの添加材２０を攪拌させたＡｌ−Ｃｕ系において、ＧＰゾーン（Guinier-Preston zone)による強化を顕著にするには、さらに第３元素として、Ｍｇを添加する方法がある。
(Combination of other additives using Al as the metal base material)
In the Al-Cu system in which the Cu additive 20 is stirred in the Al metal base materials 1a and 1b described above, in order to make the strengthening by the GP zone (Guinier-Preston zone) remarkable, Mg is further added as a third element. There is a method of adding.
また、この他にも種々の組み合わせが可能であり、例えば、Ａｌの金属母材１ａ，１ｂにＳｉの添加材２０を攪拌させたＡｌ−Ｓｉ系においては、共晶点の１２％Ｓｉ付近の組成が特性も良く頻繁に使用される。しかし、この組み合わせにおいては、溶解、鋳造時にＳｉが過冷しやすく、粗大がＳｉが晶出しやすいことから、ＮａやＳｒ等の添加による改良処理が必要であるが、本手法では、固体でプロセスが行われるため、このような問題は起こらないばかりか、回転ツール１００による攪拌作用により、Ｓｉの微細化が図れ、非常に良好な機械的特性が得られる。 In addition, various combinations are possible. For example, in the Al-Si system in which the Si metal additive 1a, 1b is stirred with the Si additive 20, the eutectic point is near 12% Si. The composition has good characteristics and is frequently used. However, in this combination, Si is likely to be supercooled during melting and casting, and Si is likely to crystallize due to coarseness. Therefore, an improvement treatment by adding Na or Sr is necessary. Therefore, not only such a problem does not occur, but also by the stirring action by the rotary tool 100, Si can be miniaturized and very good mechanical characteristics can be obtained.
この他にも、１０％程度までのＭｇを添加することで、耐食性、強さ、伸びが向上することが可能である。α固溶体とβ相（Ａｌ３Ｍｇ２）とが４５１℃で共晶関係にあり、この組み合わせでは、低比重で被削性も向上する。 In addition, corrosion resistance, strength, and elongation can be improved by adding up to about 10% Mg. The α solid solution and the β phase (Al 3 Mg 2 ) are in a eutectic relationship at 451 ° C., and this combination improves the machinability at a low specific gravity.
２種類以上の粉末等を添加する場合を考えると、ＭｇとＳｉを加えた、Ａｌ−Ｍｇ−Ｓｉ系（例えば１質量％Ｍｇ、０．６質量％Ｓｉ）、ＣｕとＭｇを加えたＡｌ−Ｃｕ−Ｍｇ系（例えば４質量％Ｃｕ、０．５質量％Ｍｇ）、さらにＭｎを加えたＡｌ−Ｃｕ−Ｍｇ−Ｍｎ系（例えば、（４質量％Ｃｕ、０．５質量％Ｍｇ、０．５質量％Ｍｎ）（４．５質量％Ｃｕ，１．５質量％Ｍｇ，０．６質量％Ｍｎ）など）、さらにＳｉを加えたＡｌ−Ｃｕ−Ｓｉ−Ｍｎ−Ｍｇ系（例えば、４．４質量％Ｃｕ，０．８質量％Ｓｉ，０．８質量％Ｍｎ，０．４質量％Ｍｇ）、ＺｎとＭｇを加えたＡｌ−Ｚｎ−Ｍｇ系、Ｃｕ、Ｎｉ、Ｍｇを加えたＡｌ−Ｃｕ−Ｎｉ−Ｍｇ（例えば、４質量％Ｃｕ，２質量％Ｎｉ，１．５質量％Ｍｇ）系等が有効である。Ｍｇ２Ｓｉ、ＣｕＡｌ２、Ａｌ５Ｃｕ２Ｍｇ、Ａｌ２ＣｕＭｇ、ＭｇＺｎ２、Ａｌ２Ｍｇ３Ｚｎ３等の化合物を微細に析出させることにより、高強度化できるが、本実施形態の処理においては、熱処理を行わなくても、条件の最適化をすることによりこれを達成することができるのが特長である。（もちろん、必要に応じて熱処理を併用するのは問題ない。） Considering the case where two or more kinds of powders are added, Al—Mg—Si system (for example, 1 mass% Mg, 0.6 mass% Si) with addition of Mg and Si, Al—with addition of Cu and Mg, Cu-Mg system (for example, 4 mass% Cu, 0.5 mass% Mg), and Al-Cu-Mg-Mn system (for example, (4 mass% Cu, 0.5 mass% Mg,. 5% by mass Mn) (4.5% by mass Cu, 1.5% by mass Mg, 0.6% by mass Mn, etc.), and further Si-added Al—Cu—Si—Mn—Mg system (for example, 4. 4 mass% Cu, 0.8 mass% Si, 0.8 mass% Mn, 0.4 mass% Mg), Al—Zn—Mg based with addition of Zn and Mg, Al—with addition of Cu, Ni and Mg A Cu—Ni—Mg (for example, 4 mass% Cu, 2 mass% Ni, 1.5 mass% Mg) system or the like is effective. The strength can be increased by finely depositing a compound such as Mg 2 Si, CuAl 2 , Al 5 Cu 2 Mg, Al 2 CuMg, MgZn 2 , Al 2 Mg 3 Zn 3, etc. The feature is that this can be achieved by optimizing the conditions without performing heat treatment. (Of course, there is no problem if heat treatment is used together if necessary.)
（Ｆｅを金属母材とした他の添加材の組合せ）
一方、鉄系材料においては、実施例の他に以下のような組み合わせも考えられる。例えば、鋳鉄において、焼き入れ性を向上させるのはＣのみではなく、部分的に、Ｃｒ、Ｍｏ、Ｎｉ、Ｖ、Ｃｕ等添加して、焼き入れ性を向上させる方法もある。
(Combination of other additives using Fe as a metal matrix)
On the other hand, in the case of iron-based materials, the following combinations can be considered in addition to the examples. For example, in cast iron, there is a method of improving the hardenability by adding not only C but also Cr, Mo, Ni, V, Cu, etc., to improve the hardenability.
この他の鉄系材料においても、例えば、オーステナイト系鋼にＣｒ、Ｍｏ、Ｓｉ、Ｎｂ、Ｖ、Ｗ、Ｔｉ、Ｔａ、Ａｌ等のフェライト安定化元素を添加して、部分的にフェライト化したり、逆にフェライト系鋼に、Ｎｉ、Ｃ、Ｎ、Ｍｎ、Ｃｏ、Ｃｕ等のオーステナイト安定化元素を添加して、部分的にオーステナイト化することも可能である。また、それを急冷して、マルテンサイト化することもあり得る。 Also in other iron-based materials, for example, by adding a ferrite stabilizing element such as Cr, Mo, Si, Nb, V, W, Ti, Ta, Al to austenitic steel, and partially ferritized, Conversely, austenite stabilizing elements such as Ni, C, N, Mn, Co, and Cu can be added to ferritic steel to partially austenite. In addition, it can be rapidly cooled to martensite.
このように、本実施形態の手法では、使用者のニーズに合わせて、大型構造物の一部の特性を容易にかつ安定的に変化させることが可能である。 As described above, according to the method of the present embodiment, it is possible to easily and stably change some characteristics of the large structure in accordance with the needs of the user.
（Ｃｕを金属母材とした他の添加材の組合せ）
Ｃｕ合金の場合には、回転ツール１００にＳＫＤ６１等の工具鋼を用いて行うことも可能であるが、耐久性を考えると、ＷＣ系合金の超硬合金等を用いることが望ましい。
(Combination of other additives using Cu as a metal base material)
In the case of a Cu alloy, it is possible to use a tool steel such as SKD61 for the rotary tool 100, but considering durability, it is desirable to use a WC alloy cemented carbide or the like.
Ｚｎを添加することで、良好な機械的特性、耐食性、高耐高温酸化性を向上させ、光沢も良い表面が得られる。例えば、Ｚｎを３０〜４０％とするのが適量である。Ｚｎが３８％以下であれば、面心立方格子型のα黄銅となり、それを超えると、（α＋β）黄銅となる。一方、Ｚｎが３５％を超えるとβ相が出現する可能性があり、β相が出現すると、硬さと強さを急激に増加させること可能である。 By adding Zn, it is possible to improve the mechanical properties, corrosion resistance, high-temperature oxidation resistance, and obtain a surface with good gloss. For example, it is appropriate that Zn is 30 to 40%. If Zn is 38% or less, it becomes a face-centered cubic lattice type α brass, and if it exceeds that, it becomes (α + β) brass. On the other hand, when Zn exceeds 35%, the β phase may appear, and when the β phase appears, the hardness and strength can be rapidly increased.
複数元素を入れる例として、Ｃｕを５４〜６２質量％、Ｚｎを３０〜４０質量％、Ａｌを０〜４質量％、Ｍｎを０〜５質量％、Ｆｅを０〜２質量％、Ｓｎを０〜１質量％、Ｐｂを０〜０．５質量％、Ｎｉを０〜１質量％添加することにより、ブリネル硬さを１１０〜１７０、引張強度を４５０〜７５０ＭＰａ、０．２％耐力を２２０〜４４０ＭＰａ、伸びを３５〜１２％の範囲に変化させることが可能である。 As an example of adding multiple elements, Cu is 54 to 62 mass%, Zn is 30 to 40 mass%, Al is 0 to 4 mass%, Mn is 0 to 5 mass%, Fe is 0 to 2 mass%, Sn is 0 -1% by mass, Pb 0-0.5% by mass, Ni 0-1% by mass, Brinell hardness 110-170, tensile strength 450-750MPa, 0.2% proof stress 220- It is possible to change the elongation to 440 MPa and the range of 35 to 12%.
特にＮｉを添加すると（例えば、Ｃｕ４８．６質量％、Ｚｎ３９．５質量％、Ｍｎ０．３３質量％、Ｆｅ２．８質量％、Ａｌ０．４８質量％、Ｎｉ８．０質量％）、β相の多くない高強度合金が得られ、極めて剛性の高い合金が得られる。 Particularly when Ni is added (for example, Cu 48.6% by mass, Zn 39.5% by mass, Mn 0.33% by mass, Fe 2.8% by mass, Al 0.48% by mass, Ni 8.0% by mass), there is not much β phase. A high strength alloy is obtained, and an extremely high rigidity alloy is obtained.
また、Ｚｎが増加すると、脱亜鉛腐食が生ずるが、これを防ぐ為には、Ｚｎ量を３０質量％以下にするか、ＡｓまたはＳｎ等を１質量％程度の少量添加することで防ぐことが可能である。 Further, when Zn increases, dezincification corrosion occurs, but in order to prevent this, it is possible to prevent it by making the amount of Zn 30% by mass or less or adding a small amount of As or Sn or the like of about 1% by mass. Is possible.
一方、Ｓｎを添加した場合には、Ｚｎを添加した場合と比較して、耐食性、耐摩耗性をさらに向上させることが可能である。Ｃｕ−Ｓｎ系は凝固温度範囲が非常に長く、一旦溶解すると、凝固時に偏析が起こりやすいが、本手法は固相で行われるため、このような問題は起こらないのが特長である。 On the other hand, when Sn is added, it is possible to further improve the corrosion resistance and wear resistance as compared with the case where Zn is added. The Cu—Sn system has a very long solidification temperature range, and once it is dissolved, segregation is likely to occur during solidification. However, since this method is performed in a solid phase, such a problem does not occur.
Ｓｎを添加することにより、耐食性が向上する。また、耐海水性も向上し、１０質量％Ｓｎまでは、Ｓｎ量が増加するにつれ向上する。例えば、１２質量％Ｓｎを添加することにより、７００℃焼き鈍し材でも、ブリネル硬さを４０から８０へ、引張強度が２５０ＭＰａから４５０ＭＰａへ向上させることが可能である。また、Ｓｎを添加することによって、色が変色し、青銅となる。また、着色のために、３〜５質量％程度のＰｂを含有させるのも効果的である。 By adding Sn, the corrosion resistance is improved. Moreover, seawater resistance is also improved and it improves as Sn amount increases to 10 mass% Sn. For example, by adding 12 mass% Sn, it is possible to improve the Brinell hardness from 40 to 80 and the tensile strength from 250 MPa to 450 MPa even with a 700 ° C. annealed material. Further, by adding Sn, the color is changed to become bronze. Moreover, it is also effective to contain about 3-5 mass% Pb for coloring.
Ｓｎ量が１５質量％超えるとδ相が析出し、硬度を上昇させることが可能である。また、０．０５〜０．５質量％のＰを添加することにより、合金の硬さ、強さが増加し、耐摩耗性、弾性が改善される。通常は、このような組成で溶解、鋳造では偏析が起こりやすいが、本手法では、溶解を伴わないので、容易に作製することが可能である。一方、鉛を４〜２２質量％入れると、潤滑性が向上する。この場合も、溶解法では逆偏析が起こりやすいが、本プロセスではそのような問題は生じない。 When the Sn amount exceeds 15% by mass, the δ phase is precipitated, and the hardness can be increased. Moreover, the addition of 0.05 to 0.5% by mass of P increases the hardness and strength of the alloy and improves the wear resistance and elasticity. Usually, segregation is likely to occur during melting and casting with such a composition, but in this method, since melting does not occur, it can be easily produced. On the other hand, when 4 to 22 mass% of lead is added, lubricity is improved. Also in this case, reverse segregation is likely to occur in the melting method, but such a problem does not occur in the present process.
また、本プロセスのみで硬化が十分でない場合には、熱処理を併用することもむろん可能である。例えば、Ｃｕ−２０質量％Ｓｎ合金を２００〜３５０℃で熱処理すると硬化し、例えば、７５０℃より焼き入れ後、３００℃で焼き戻しすると、ブリネル硬さが１６１から２１２へ上昇する。 In addition, when curing is not sufficient only by this process, it is of course possible to use heat treatment together. For example, when a Cu-20 mass% Sn alloy is heat-treated at 200 to 350 ° C, it hardens. For example, after quenching from 750 ° C and tempering at 300 ° C, the Brinell hardness increases from 161 to 212.
さらに、複数元素の添加例として、ＮｉとＳｎを添加した場合（例えば、Ｃｕ：Ｎｉ：Ｓｎ＝８９：９：２に調整すると）、スピノーダル分解を起こし、Ｎｉ３Ｓｎの析出し、Ａｌ−Ｃｕ系と同様な効果が得られる。さらに、これにＺｎを添加した場合、（例えば、Ｃｕ：Ｎｉ：Ｓｎ：Ｚｎ＝８８：５：５：２の場合）、引張強さは６００ＭＰａ以上、ブリネル硬さは１７０以上となる。 Furthermore, as an example of addition of multiple elements, when Ni and Sn are added (for example, when adjusted to Cu: Ni: Sn = 89: 9: 2), spinodal decomposition occurs, Ni 3 Sn precipitates, and Al—Cu The same effect as the system can be obtained. Further, when Zn is added to this (for example, Cu: Ni: Sn: Zn = 88: 5: 5: 2), the tensile strength is 600 MPa or more and the Brinell hardness is 170 or more.
次に、Ｃｕの金属母材にＡｌを添加した場合について述べる。Ａｌを９．０〜１５．６質量％添加すると、鋼と同様なパーライトと同様な層状共析組織になり、良好な機械的特性が得られ、急冷するとマルテンサイト、ベイナイト組織が得られる。 Next, a case where Al is added to a Cu metal base material will be described. When 9.0 to 15.6% by mass of Al is added, a layered eutectoid structure similar to that of pearlite similar to steel is obtained, and good mechanical properties are obtained. When quenched, martensite and bainite structures are obtained.
これに、他の元素を添加し、３元系とするとさらに良い特性が得られる。例えば、Ｆｅが固溶限以上に添加するとκ相（ＦｅＡｌ）が析出するが、３．５質量％以上添加すると、β相の微細化に効果を発揮する。また、Ｎｉも４〜５質量％の添加で同様な効果が期待できる。ＮｉとＦｅが共に４〜５質量％、Ａｌが９．５〜９．８質量％とすると、最も良好な機械的特性が得られる。特に、強さ、耐摩耗性、耐食性、耐浸食性にすぐれ、特に耐浸食性に関しては、高Ｃｒステンレス鋳物より優れる。 When other elements are added to this to form a ternary system, even better characteristics can be obtained. For example, when Fe is added to the solid solubility limit or more, the κ phase (FeAl) is precipitated. However, when 3.5 mass% or more is added, the effect of refinement of the β phase is exhibited. Moreover, the same effect can be expected when Ni is added in an amount of 4 to 5% by mass. When both Ni and Fe are 4 to 5% by mass and Al is 9.5 to 9.8% by mass, the best mechanical properties are obtained. In particular, it excels in strength, wear resistance, corrosion resistance, and erosion resistance, and in particular, it is superior to high Cr stainless steel castings in terms of erosion resistance.
また、Ｃｕに２．５質量％までのＢｅ、おおよそ２質量％程度のＢｅを添加すると、γ（ＣｕＢｅ）が析出し、強さ、耐摩耗性、導電率が向上する。４質量％Ｂｅではブリネル硬さが５００を超えることがある。 Further, when up to 2.5 mass% Be or about 2 mass% Be is added to Cu, γ (CuBe) is precipitated, and the strength, wear resistance, and conductivity are improved. At 4 mass% Be, the Brinell hardness may exceed 500.
（Ｍｇを金属母材とした添加材の組合せ）
Ｍｇに対しては、ＡｌあるはＺｎあるいは両方を添加するのが有効である。これらでは、固溶強化の他に、Ｍｇ１７Ａｌ１２やＡｌ２Ｍｇ３Ｚｎ３等の析出物によって、機械的特性の向上が図られる。また、２％程度のＣａを添加することにより、難燃性へと変化する。
(Combination of additives using Mg as a metal matrix)
For Mg, it is effective to add Al or Zn or both. In these, in addition to solid solution strengthening, mechanical properties are improved by precipitates such as Mg 17 Al 12 and Al 2 Mg 3 Zn 3 . Moreover, it changes to a flame retardance by adding about 2% of Ca.
（Ｔｉを金属母材とした添加材の組合せ）
Ｔｉには、Ａｌ、Ｓｎ、Ｍｎ、Ｆｅ、Ｃｒ、Ｍｏ、Ｖ等を添加すると、機械的特性を向上させることができる。これらは、チタンのα相を安定化させるものと、β相を安定化するものに分けられ、Ａｌは前者に分類される。α相の強化を図るものは、固溶強化である。α相はちゅう密六方型結晶であるので、塑性変形能は低下するが、高温強さが向上し、クリープ特性が改善される（強いα＋強いβ）。
(Combination of additives using Ti as a metal base material)
When Al, Sn, Mn, Fe, Cr, Mo, V, or the like is added to Ti, the mechanical properties can be improved. These are classified into those that stabilize the α phase of titanium and those that stabilize the β phase, and Al is classified as the former. What strengthens the α phase is solid solution strengthening. Since the α phase is a dense hexagonal crystal, the plastic deformability is reduced, but the high-temperature strength is improved and the creep properties are improved (strong α + strong β).
一方、β相を安定化した、例えば、７質量％Ｍｎ合金では、β相を強化し、α相の靱性をあまり損じないから、合金の加工性がよく、圧延して板材などにつくることに適する（強いβ＋粘りがあるα）。 On the other hand, for example, a 7% by mass Mn alloy with a stabilized β phase strengthens the β phase and does not significantly impair the toughness of the α phase. Suitable (strong β + sticky α).
合金の種類を列記すると以下の通りである。
α安定化型合金：Ａｌ、Ｓｎ、Ｏ、Ｎ
β共析型合金：Ｍｎ、Ｃｒ、Ｆｅ、Ｎｉ、Ｃｏ、Ｃｕ、Ａｇ、Ｐｂ、Ｓｉ、Ｗ
β固溶体型合金：Ｍｏ、Ｖ、Ｎｂ、Ｔａ
α、β全率固溶体型合金：Ｚｒ
The types of alloys are listed as follows.
α-stabilized alloy: Al, Sn, O, N
β eutectoid alloy: Mn, Cr, Fe, Ni, Co, Cu, Ag, Pb, Si, W
β solid solution type alloys: Mo, V, Nb, Ta
α, β total solid solution type alloy: Zr
また、β相から急冷させ、β相を残留させて熱処理効果が期待できる合金にＦｅ、Ｍｇ、Ｃｒ、Ｍｎなどである。本実施形態の処理では、条件を最適化することにより、熱処理なしで同様な効果が得られる。 Also, Fe, Mg, Cr, Mn and the like are alloys that can be rapidly cooled from the β phase and remain in the β phase to expect a heat treatment effect. In the processing of this embodiment, the same effect can be obtained without heat treatment by optimizing the conditions.
本実施形態によれば、金属母材１ａ，１ｂとは異なる組成であり、且つ金属母材１ａ，１ｂとの化学反応を生じる添加材１０を、金属母材１ａ，１ｂの一部である攪拌部２０に配置し、攪拌部２０に棒状の回転ツール１００の先端を当接させつつ回転させるため、摩擦攪拌接合の手法を利用した一つの方法で、金属母材１ａ，１ｂの所望の部位に対して添加材１０の分散、拡散及び析出あるいは分散、拡散及び変態といった合金を製造する３つの過程を実現することができる。そのため、金属母材１ａ，１ｂの所望の部位を所望の組成の金属とすることが可能となる。特に、摩擦攪拌接合の手法により、従来、熟練を要していた焼入れ作業等をより速く行なうことができる。特に、大型の金属構造物の一部の硬度を高めたいときに、本実施形態の方法は効果を発揮する。 According to this embodiment, the additive 10 having a composition different from that of the metal base materials 1a and 1b and causing a chemical reaction with the metal base materials 1a and 1b is stirred as a part of the metal base materials 1a and 1b. In order to rotate the agitator 20 while the tip of the rod-shaped rotary tool 100 is in contact with the agitator 20, it is applied to a desired part of the metal base materials 1 a and 1 b by one method using the friction agitation welding method. On the other hand, three processes for producing an alloy such as dispersion, diffusion and precipitation or dispersion, diffusion and transformation of the additive 10 can be realized. Therefore, it becomes possible to make a desired portion of the metal base materials 1a and 1b a metal having a desired composition. In particular, by the friction stir welding method, conventionally hardened work and the like that required skill can be performed more quickly. In particular, when it is desired to increase the hardness of a part of a large metal structure, the method of this embodiment is effective.
特に、本実施形態によれば、金属母材１ａ，１ｂ中に添加材１０を攪拌、拡散、及び析出させることにより、特に金属母材１ａ，１ｂがＡｌであり、添加材１０がＣｕである場合に、金属母材１ａ，１ｂの所望の部位をさらに優れた特性の金属とすることが可能となる。 In particular, according to the present embodiment, by stirring, diffusing and precipitating the additive material 10 in the metal base materials 1a and 1b, the metal base materials 1a and 1b are particularly Al and the additive material 10 is Cu. In this case, the desired parts of the metal base materials 1a and 1b can be made a metal having further excellent characteristics.
あるいは、本実施形態によれば、金属母材中１ａ，１ｂに添加材１０を攪拌、拡散、及び変態させることにより、特に金属母材１ａ，１ｂがＦｅであり、添加材１０がＣである場合に、金属母材１ａ，１ｂの所望の部位をさらに優れた特性の金属とすることが可能となる。 Alternatively, according to the present embodiment, the metal base materials 1a and 1b are particularly Fe and the additive material 10 is C by stirring, diffusing and transforming the additive material 10 in the metal base materials 1a and 1b. In this case, the desired parts of the metal base materials 1a and 1b can be made a metal having further excellent characteristics.
さらに、本実施形態によれば、金属母材１ａ，１ｂはＡｌを含むものとし、添加材１０はＣｕを含むものとするため、ＡｌとＣｕとの合金であるジュラルミンを金属母材１ａ，１ｂの所望の部位に製造することが可能となる。 Furthermore, according to the present embodiment, since the metal base materials 1a and 1b include Al and the additive 10 includes Cu, duralumin, which is an alloy of Al and Cu, is used as a desired metal base material 1a and 1b. It becomes possible to manufacture the part.
また、本実施形態によれば、攪拌部２０に回転ツール１００を少なくとも２回通過させるため、攪拌部２０の状態をより良好なものとすることができる。 Moreover, according to this embodiment, since the rotary tool 100 is passed through the stirring unit 20 at least twice, the state of the stirring unit 20 can be made better.
また、本実施形態によれば、回転ツール１００のプローブ１０２の径ｒがｒ≧２ｗと攪拌部の幅ｗに対して十分に大きいため、攪拌部の状態をより良好なものとすることができる。 Moreover, according to this embodiment, since the diameter r of the probe 102 of the rotary tool 100 is sufficiently larger than r ≧ 2w and the width w of the stirring unit, the state of the stirring unit can be improved. .
さらに、本実施形態によれば、添加材１０を金属母材１ａ，１ｂの攪拌部２０に配置する工程では、攪拌部２０に金属母材１ａ，１ｂ及び添加材１０とは異なる物質を少なくとも１種類以上さらに配置することにより、金属母材１ａ，１ｂと添加材１０との２種類の物質からなる金属材のみならず、３種類以上の物質からなる金属材も製造することが可能である。 Furthermore, according to the present embodiment, in the step of placing the additive 10 in the stirring part 20 of the metal base materials 1a, 1b, at least one substance different from the metal base materials 1a, 1b and the additive 10 is added to the stirring part 20. By arranging more than one kind, it is possible to produce not only a metal material composed of two kinds of materials, ie, the metal base materials 1a and 1b and the additive material 10, but also a metal material composed of three or more kinds of substances.
また、本実施形態によれば、粉状、粒状及び板状のいずれかの添加材１０を攪拌部２０に配置するため、攪拌部２０において製造される金属材の組成を制御することがより容易になる。 Moreover, according to this embodiment, since the powdery, granular, or plate-like additive 10 is disposed in the stirring unit 20, it is easier to control the composition of the metal material produced in the stirring unit 20. become.
加えて、本実施形態によれば、粉状の添加材１０は複数の種類の粉状又は粒状の物質の混合物及び複数種類の板状の物質の積層物からなるものとし、複数の種類の物質の割合を変更することにより、製造される金属材の性質を変更するため、攪拌部２０において製造される金属材の組成を制御することがさらに容易になり、所望の性質の金属材を製造することがさらに容易となる。 In addition, according to this embodiment, the powdery additive 10 is composed of a mixture of a plurality of types of powdery or granular substances and a laminate of a plurality of types of plate-like substances, and a plurality of types of substances. By changing the ratio, the property of the metal material to be produced is changed, so that it becomes easier to control the composition of the metal material produced in the stirring unit 20, and a metal material having a desired property is produced. It becomes even easier.
以下、本発明の第２実施形態について説明する。図３４に示すように、本実施形態では、板状の金属母材１ａと板状の添加材１１とを端部同士で突き合せるか、近接させて攪拌部２０とする。板状の金属母材１ａあるいは板状の添加材１１としては、上記第１実施形態と同様とすることができる。次に、図３５に示すように、攪拌部２０に回転ツール１００を当接させつつ回転させ、回転ツール１００を攪拌部２０の長手方向に沿って移動させることにより、金属母材１ａと添加材１１とを接合する。これにより、金属母材１ａと添加材２０とを接合させた上で、金属母材１ａと添加材１１との接合部となる攪拌部２０を所望の組成の金属材とすることが可能となる。なお、本実施形態の態様においても、図４及び図５に示すようなスポット型の摩擦攪拌処理、図６〜８に示したような重ね合わせ接合に類似の摩擦攪拌処理を行うものとできる。 Hereinafter, a second embodiment of the present invention will be described. As shown in FIG. 34, in this embodiment, the plate-shaped metal base material 1a and the plate-shaped additive 11 are abutted with each other or brought close together to form the stirring unit 20. The plate-like metal base material 1a or the plate-like additive 11 can be the same as that in the first embodiment. Next, as shown in FIG. 35, the rotating tool 100 is rotated while being in contact with the stirring unit 20, and the rotating tool 100 is moved along the longitudinal direction of the stirring unit 20, whereby the metal base material 1 a and the additive material are moved. 11 is joined. Thereby, after joining the metal base material 1a and the additive material 20, it becomes possible to make the stirring part 20 used as the junction part of the metal base material 1a and the additive material 11 into a metal material of a desired composition. . Note that, in the aspect of the present embodiment as well, a spot-type friction stir processing as shown in FIGS. 4 and 5 and a friction stir processing similar to the superposition joining as shown in FIGS.
あるいは、図３６に示すように、板状の金属母材１ａ及び板状の添加材１１の間に、金属母材１ａ及び添加材１１の両方の組成を含む中間材１２を配置して、攪拌部２０とし、図３７に示すように、攪拌部２０に対して摩擦攪拌処理を行っても良い。この態様では、添加材１１及び金属母材１ａの両方の組成を含む中間材１２を添加材１１と金属母材１ａとの間に配置し、中間材１２を配置した箇所を攪拌部２０とするため、金属母材１ａと中間材１２との生成物及び添加材１１と中間材１２との生成物が厚く生成されることが抑制されるため、より良好な攪拌部２０とすることが可能となる。 Alternatively, as shown in FIG. 36, an intermediate material 12 including the composition of both the metal base material 1a and the additive material 11 is disposed between the plate-shaped metal base material 1a and the plate-like additive material 11, and stirring is performed. As shown in FIG. 37, friction stirring processing may be performed on the stirring unit 20 as the unit 20. In this aspect, the intermediate material 12 including the composition of both the additive material 11 and the metal base material 1a is disposed between the additive material 11 and the metal base material 1a, and the portion where the intermediate material 12 is disposed is used as the stirring unit 20. Therefore, since it is suppressed that the product of the metal base material 1a and the intermediate material 12 and the product of the additive material 11 and the intermediate material 12 are generated thick, it is possible to make the stirring unit 20 better. Become.
尚、本発明は、上記した実施の形態に限定されるものではなく、本発明の要旨を逸脱しない範囲内において種々変更を加え得ることは勿論である。 It should be noted that the present invention is not limited to the above-described embodiment, and it is needless to say that various modifications can be made without departing from the gist of the present invention.
１ａ，１ｂ…金属母材、１０，１０ａ，１０ｂ…添加材、１１…異種金属材、１２…中間材、２０…攪拌部、１００…回転ツール、１０１…ショルダー、１０２…プローブ。 DESCRIPTION OF SYMBOLS 1a, 1b ... Metal base material, 10, 10a, 10b ... Additive material, 11 ... Dissimilar metal material, 12 ... Intermediate material, 20 ... Stirring part, 100 ... Rotary tool, 101 ... Shoulder, 102 ... Probe.
Claims (12)
前記金属母材とは異なる組成であり、且つ前記金属母材との化学反応を生じる添加材を、前記金属母材の一部である攪拌部に配置する工程と、
前記攪拌部に棒状の回転ツールの先端を当接させつつ回転させる工程と、
を含む金属材の製造方法。 Preparing a metal base material;
A step of disposing an additive having a composition different from that of the metal base material and causing a chemical reaction with the metal base material in a stirring portion that is a part of the metal base material;
Rotating while abutting the tip of a rod-shaped rotating tool to the stirring unit;
The manufacturing method of the metal material containing this.
前記攪拌部に棒状の回転ツールを当接させつつ回転させる工程では、前記攪拌部に前記回転ツールを当接させつつ回転させることにより、前記金属母材と前記添加材とを接合する、請求項１〜７のいずれか１項に記載の金属材の製造方法。 In the step of placing the additive in the stirring portion of the metal base, the end of the additive is brought into contact with or close to the metal base and the end of the additive is brought into contact or close The portion that has been made the stirring section,
The step of rotating the agitating part while abutting a rod-shaped rotating tool joins the metal base material and the additive by rotating the agitating part while abutting the rotating tool. The manufacturing method of the metal material of any one of 1-7.
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