JPH0940476A - Joined body of aluminum alloy member and ceramic member - Google Patents
Joined body of aluminum alloy member and ceramic memberInfo
- Publication number
- JPH0940476A JPH0940476A JP11015296A JP11015296A JPH0940476A JP H0940476 A JPH0940476 A JP H0940476A JP 11015296 A JP11015296 A JP 11015296A JP 11015296 A JP11015296 A JP 11015296A JP H0940476 A JPH0940476 A JP H0940476A
- Authority
- JP
- Japan
- Prior art keywords
- aluminum alloy
- ceramic
- joined body
- thickness
- ceramic member
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、アルミニウム合金部材
とセラミックス部材との接合体に関し、更に詳しくは自
動車、航空機、鉄道車両等に用いられる構造部材や超音
波加工に用いられるホーンに代表される加工工具等の産
業部品に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a joined body of an aluminum alloy member and a ceramic member, and more specifically, it is represented by a structural member used in automobiles, aircrafts, railway vehicles and the like, and a horn used in ultrasonic machining. Related to industrial parts such as processing tools.
【０００２】[0002]
【従来の技術】アルミニウム又はその合金は、一般の鉄
系材料に比べて軽量、高熱伝導、高電気伝導、高耐食性
などの利点を有する。特に時効硬化型アルミニウム合金
であるＪＩＳ２０００系のアルミニウム合金、ＪＩＳ６
０００系のアルミニウム合金、ＪＩＳ７０００系のアル
ミニウム合金は熱処理により高い材料強度が得られるた
め、構造部材として広く用いられている。一方、セラミ
ックス材料は耐摩耗性、耐食性、耐熱性に優れるためア
ルミニウム合金と複合化することにより優れた機能を具
備せしめることが可能となる。かかる複合化の手段とし
ては、鋳ぐるみやろう付接合が一般的に知られている。2. Description of the Related Art Aluminum or its alloy has advantages such as light weight, high heat conduction, high electric conduction and high corrosion resistance as compared with general iron-based materials. In particular, JIS2000 series aluminum alloy, JIS6, which is an age hardening type aluminum alloy.
000 series aluminum alloys and JIS 7000 series aluminum alloys are widely used as structural members because high material strength can be obtained by heat treatment. On the other hand, ceramic materials are excellent in wear resistance, corrosion resistance, and heat resistance, so that they can be provided with excellent functions by combining with an aluminum alloy. As a means for forming such a composite, cast dolls and brazing are generally known.
【０００３】[0003]
【発明が解決しようとする課題】しかし、セラミックス
部材を鋳ぐるみした複合体は、アルミニウム合金が鋳造
のまま用いられるのでアルミニウム合金自体の強度が低
い。また、一般に鋳ぐるみしたものは圧延等の加工によ
り高強度となるが、セラミックス部材を既に鋳ぐるみし
たものは加工が困難である。一方、ろう付接合によれば
アルミニウム合金とセラミックス部材との複合化は可能
であるが、通常ろう付け接合は４００℃以上で行なわれ
るためアルミニウム合金自体が鈍ってしまい、やはりア
ルミニウム合金自体の強度が低い。このためろう付接合
の終了後に溶体化処理及び時効処理が必要となるが、通
常溶体化は４５０℃から５５０℃の温度範囲から水焼入
れすることにより行なわれ、このときアルミニウム合金
が一層硬化する。これに伴って発生する熱応力（熱膨張
差に起因する残留応力）によりセラミックス部材にクラ
ックが発生したり、接合面が剥離する等の不具合が生じ
ることがあった。この熱応力は、セラミックス材料がア
ルミニウム合金に比べ、熱膨張係数が小さいためであ
る。However, since the aluminum alloy is used as it is in the casting, the strength of the aluminum alloy itself is low. Further, in general, cast products have high strength by processing such as rolling, but it is difficult to process cast ceramic products that have already been cast. On the other hand, by brazing, an aluminum alloy and a ceramic member can be composited, but since the brazing is usually performed at 400 ° C. or higher, the aluminum alloy itself becomes dull, and the strength of the aluminum alloy itself is also low. Low. For this reason, solution treatment and aging treatment are required after the completion of brazing, but solution treatment is usually performed by water quenching from a temperature range of 450 ° C to 550 ° C, at which time the aluminum alloy is further hardened. Due to the thermal stress (residual stress resulting from the difference in thermal expansion) generated along with this, a crack may occur in the ceramic member, or a joint surface may be peeled off. This thermal stress is because the ceramic material has a smaller coefficient of thermal expansion than the aluminum alloy.
【０００４】本発明の課題は、高強度なアルミニウム合
金部材とセラミックス部材とが強固に接合された接合体
を提供することである。An object of the present invention is to provide a joined body in which a high-strength aluminum alloy member and a ceramic member are firmly joined.
【０００５】[0005]
【課題を解決するための手段及び作用】その第１の手段
は、時効硬化型アルミニウム合金部材とセラミックス部
材とが非熱処理型アルミニウム合金からなる中間部材を
介して接合されているアルミニウム合金部材とセラミッ
クス部材との接合体である。第１の手段の接合体は、溶
体化処理（焼入れ）により又は使用時の熱間において
も、時効硬化型アルミニウム合金は硬化するが非熱処理
型アルミニウム合金は硬化しない。従って非熱処理型ア
ルミニウム合金からなる中間部材は、時効処理型アルミ
ニウム合金部材とセラミックス部材との間で応力緩衝層
として有効に機能する。更に部材間に生ずる各部材の熱
膨張係数の差に起因するセラミックス部材に発生するク
ラックや、中間部材とセラミックス部材との接合面の剥
離を防止することができる。その第２の手段は、時効硬
化型アルミニウム合金部材とセラミックス部材とが非熱
処理型アルミニウム合金からなる中間部材を２以上介し
て接合されているアルミニウム合金部材とセラミックス
部材との接合体である。第２の手段の接合体は、第１の
手段の接合体と同様の作用を有する他に中間部材の数が
多い分、更に中間部材が応力緩衝層として有効に機能
し、部材間に生ずる各部材の熱膨張係数の差に起因する
セラミックス部材に発生するクラックや、中間部材とセ
ラミックス部材との接合面の剥離を防止することができ
る。[Means and Action for Solving the Problems] The first means thereof is an aluminum alloy member and a ceramic in which an age hardening type aluminum alloy member and a ceramic member are joined via an intermediate member made of a non-heat treatment type aluminum alloy. It is a joined body with a member. In the joined body of the first means, the age hardening type aluminum alloy is hardened but the non-heat treatment type aluminum alloy is not hardened by solution treatment (quenching) or even during hot use. Therefore, the intermediate member made of the non-heat treatment type aluminum alloy effectively functions as a stress buffer layer between the aging treatment type aluminum alloy member and the ceramic member. Further, it is possible to prevent cracks occurring in the ceramic member due to the difference in the thermal expansion coefficient of each member between the members and peeling of the joint surface between the intermediate member and the ceramic member. The second means is a joined body of an aluminum alloy member and a ceramic member in which the age hardening type aluminum alloy member and the ceramic member are joined via two or more intermediate members made of a non-heat treatment type aluminum alloy. The joined body of the second means has the same function as that of the joined body of the first means, and in addition to the large number of intermediate members, the intermediate member effectively functions as a stress buffer layer, and each of the members generated between the members. It is possible to prevent cracks occurring in the ceramic member due to the difference in the coefficient of thermal expansion of the members and peeling of the joint surface between the intermediate member and the ceramic member.
【０００６】ここで時効硬化型アルミニウム合金は、例
えばＪＩＳ２０００系に規定されるＡｌ−Ｃｕ系、ＪＩ
Ｓ６０００系に規定されるＡｌ−Ｍｇ−Ｓｉ系、ＪＩＳ
７０００系に規定されるＡｌ−Ｚｎ−Ｍｇ系、あるいは
ＪＩＳＡＣ２Ａ、ＪＩＳＡＣ４Ａ等に代表される合金鋳
物，ＡＤＣ１０等に代表されるダイキャスト合金等のア
ルミニウム合金である。即ち、例えば、４００〜６００
℃程度の接合熱処理により、材料の硬さが低下し、再度
溶体化及び時効硬化処理を必要とするようなアルミニウ
ム合金である。また非熱処理型アルミニウム合金は、例
えばＪＩＳ１０００系に規定される純Ａｌ系、ＪＩＳ３
０００系に規定されるＡｌ−Ｍｎ系、ＪＩＳ４０００系
に規定されるＡｌ−Ｓｉ系、ＪＩＳ５０００系に規定さ
れるＡｌ−Ｍｇ系のアルミニウム合金である。前記非熱
処理型アルミニウム合金は、Ａｌ−Ｍｇ系合金であるこ
とが好ましい。それは、例えばＪＩＳ５０００系のＡｌ
−Ｍｇ系アルミニウム合金は、例えばＪＩＳ３０００系
のＡｌ−Ｍｎ系アルミニウム合金に比して強度が高いの
で耐力を向上させつつ応力緩和機能を維持できるからで
ある。また、前記非熱処理型アルミニウム合金は、Ａｌ
を９９重量％以上含有すること、いわゆる純Ａｌ系アル
ミニウムが好ましい。それは、Ａｌを９９重量％以上含
有する純Ａｌ系アルミニウムは、軟質であり応力緩和に
大きく寄与するからである。Here, the age hardening type aluminum alloy is, for example, Al-Cu system or JI system defined in JIS2000 system.
Al-Mg-Si system specified by S6000 system, JIS
It is an Al-Zn-Mg system defined in 7000 series, an alloy casting represented by JISAC2A, JISAC4A, etc., or an aluminum alloy such as a die cast alloy represented by ADC10, etc. That is, for example, 400 to 600
It is an aluminum alloy whose hardness is lowered by the joining heat treatment at about ° C, and which requires solution treatment and age hardening treatment again. Further, the non-heat treatment type aluminum alloy is, for example, pure Al based on JIS1000, JIS3 based.
Al-Mn-based aluminum alloys defined in 000 series, Al-Si systems defined in JIS 4000 series, and Al-Mg series aluminum alloys defined in JIS 5000 series. The non-heat treatment type aluminum alloy is preferably an Al-Mg based alloy. It is, for example, JIS 5000 series Al
This is because the -Mg-based aluminum alloy has a higher strength than, for example, the JIS3000-based Al-Mn-based aluminum alloy, and thus can improve the proof stress and maintain the stress relaxation function. The non-heat treatment type aluminum alloy is Al
Of 99% by weight or more, that is, so-called pure Al-based aluminum is preferable. This is because pure Al-based aluminum containing 99% by weight or more of Al is soft and greatly contributes to stress relaxation.
【０００７】前記中間部材の厚さは、０．１〜２．０ｍ
ｍであることが好ましい。０．１ｍｍ未満では応力緩和
機能に乏しく、２．０ｍｍを越えると効果があまり変わ
らないばかりか接合体に負荷が生じた時に中間部材に降
伏が起きることがあり好ましくない。また、前記中間部
材の厚さが、０．１〜１．０ｍｍであることが好まし
い。０．１ｍｍ未満では上記と同様に応力緩和機能に乏
しく、１ｍｍ以下であれば上記の２ｍｍ以下の場合に比
し、更に中間部材に降伏が起こりにくい。前記時効硬化
型アルミニウム合金部材の硬さがＨｖ１００以上である
接合体が好ましい。Ｈｖ１００以上とすることにより耐
力２５０ＭＰａ程度の材料強度を確保できる。ここで、
「中間部材の厚さ」は、第１の手段及び第２の手段とも
に一つの中間部材の厚さを意味する。The thickness of the intermediate member is 0.1 to 2.0 m.
m is preferable. If it is less than 0.1 mm, the stress relaxation function is poor, and if it exceeds 2.0 mm, not only the effect does not change significantly, but also the intermediate member may yield when a load is applied to the bonded body, which is not preferable. Further, the thickness of the intermediate member is preferably 0.1 to 1.0 mm. If it is less than 0.1 mm, the stress relaxation function is poor as in the above case, and if it is 1 mm or less, yielding is less likely to occur in the intermediate member as compared with the case of 2 mm or less. A joined body in which the age-hardening aluminum alloy member has a hardness of Hv100 or more is preferable. By setting the Hv to 100 or more, a material strength with a yield strength of about 250 MPa can be secured. here,
The "thickness of the intermediate member" means the thickness of one intermediate member for both the first means and the second means.
【０００８】ところで、第２の手段のように２以上の中
間部材を介した接合体は、個々の中間部材の厚みが２．
０ｍｍ以下であっても、合計した中間部材の厚みが２．
０ｍｍを越える場合がある。この場合には、個々の中間
部材が応力緩衝層として個々に機能し、部材間に生ずる
各部材の熱膨張係数の差に起因するセラミックス部材に
発生するクラックや、中間部材とセラミックス部材との
接合面の剥離を防止することができる。即ち、合計した
中間部材の厚みが２．０ｍｍを越えた場合は、個々の中
間部材の厚みが２．０ｍｍを越えた場合に比べ、中間部
材同士の接合界面が更に応力緩衝層として機能する。ま
た、第２の手段のように２以上の中間部材を介した接合
体の好ましい態様の中間部材の厚さを０．１〜１．０ｍ
ｍとした場合であっても、同様である。つまり、個々の
中間部材の厚みが１．０ｍｍ以下であっても、合計した
中間部材の厚みが１．０ｍｍを越える場合がある。この
場合には、個々の中間部材が応力緩衝層として個々に機
能し、部材間に生ずる各部材の熱膨張係数の差に起因す
るセラミックス部材に発生するクラックや、中間部材と
セラミックス部材との接合面の剥離を防止することがで
きる。即ち、合計した中間部材の厚みが１．０ｍｍを越
えた場合は、個々の中間部材の厚みが１．０ｍｍを越え
た場合に比べ、中間部材同士の接合界面が更に応力緩衝
層として機能する。またセラミックスは、例えば、Ａｌ
2Ｏ3、ＺｒＯ2、Ｓｉ3Ｎ4 、ＡｌＮ、ＳｉＣ或いはこれ
らの複合材、又は超硬、サーメット等の低膨張焼結材料
等周知の材料が使用可能である。ここで、溶体化処理と
は、高温に加熱して析出相を母相中に溶かし込み、これ
を急冷する処理をいう。By the way, in the joined body having two or more intermediate members as in the second means, the thickness of each intermediate member is 2.
Even if it is 0 mm or less, the total thickness of the intermediate members is 2.
It may exceed 0 mm. In this case, each intermediate member individually functions as a stress buffer layer, and cracks are generated in the ceramic member due to the difference in thermal expansion coefficient between the members that occurs between the members, and the joining of the intermediate member and the ceramic member. The peeling of the surface can be prevented. That is, when the total thickness of the intermediate members exceeds 2.0 mm, the joint interface between the intermediate members further functions as a stress buffer layer as compared with the case where the thickness of each intermediate member exceeds 2.0 mm. Further, the thickness of the intermediate member in a preferred embodiment of the joined body having two or more intermediate members as in the second means is 0.1 to 1.0 m.
The same applies when m is set. That is, even if the thickness of each intermediate member is 1.0 mm or less, the total thickness of the intermediate members may exceed 1.0 mm. In this case, each intermediate member individually functions as a stress buffer layer, and cracks are generated in the ceramic member due to the difference in thermal expansion coefficient between the members that occurs between the members, and the joining of the intermediate member and the ceramic member. The peeling of the surface can be prevented. That is, when the total thickness of the intermediate members exceeds 1.0 mm, the joint interface between the intermediate members further functions as a stress buffer layer as compared with the case where the thickness of each intermediate member exceeds 1.0 mm. Further, the ceramic is, for example, Al
Well-known materials such as 2 O 3 , ZrO 2 , Si 3 N 4 , AlN, SiC or composite materials thereof, or low expansion sintered materials such as cemented carbide and cermet can be used. Here, the solution treatment is a treatment in which the precipitation phase is melted in the mother phase by heating it at a high temperature, and this is rapidly cooled.
【０００９】[0009]
【発明の実施の形態】本発明の一の実施の形態を図１
（図２）に示す。アルミニウム合金部材とセラミックス
部材との接合体１は、図１に示すように時効硬化型アル
ミニウム合金部材３とセラミックス部材２とが非熱処理
型アルミニウム合金からなる中間部材４を介して接合さ
れている。本発明の他の実施の形態である接合体の接合
する直前の状態を図３に示す。アルミニウム合金部材と
セラミックス部材との接合体１は、時効硬化型アルミニ
ウム合金部材３とセラミックス部材２とを非熱処理型ア
ルミニウム合金からなる中間部材４及び中間部材８を介
して接合することにより得ることができる。本発明の他
の実施の形態である接合体の接合する直前の状態を図４
に示す。アルミニウム合金部材とセラミックス部材との
接合体１は、時効硬化型アルミニウム合金部材３とセラ
ミックス部材２とを非熱処理型アルミニウム合金からな
る中間部材４、中間部材８及び中間部材１０を介して接
合することにより得ることができる。その具体的な接合
方法は、ろう付けによる接合が好ましいが、拡散接合、
摩擦圧接、はんだ付けも可能である。また、接合後に溶
体化処理、または溶体化処理及び時効硬化処理すること
により更に強固な接合体を得ることができる。DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENT FIG. 1 shows an embodiment of the present invention.
(FIG. 2). As shown in FIG. 1, a joined body 1 of an aluminum alloy member and a ceramic member is joined with an age hardening type aluminum alloy member 3 and a ceramic member 2 via an intermediate member 4 made of a non-heat treatment type aluminum alloy. FIG. 3 shows a state immediately before joining of a joined body which is another embodiment of the present invention. The joined body 1 of the aluminum alloy member and the ceramic member is obtained by joining the age hardening type aluminum alloy member 3 and the ceramic member 2 via the intermediate member 4 and the intermediate member 8 made of the non-heat treatment type aluminum alloy. it can. FIG. 4 shows a state immediately before joining of a joined body according to another embodiment of the present invention.
Shown in The joined body 1 of the aluminum alloy member and the ceramic member is formed by joining the age hardening type aluminum alloy member 3 and the ceramic member 2 via the intermediate member 4, the intermediate member 8 and the intermediate member 10 made of the non-heat treatment type aluminum alloy. Can be obtained by The specific joining method is preferably joining by brazing, but diffusion joining,
Friction welding and soldering are also possible. Further, a stronger joint can be obtained by performing solution treatment or solution treatment and age hardening treatment after joining.
【００１０】ー実験例１ー セラミックス部材２として表１に示す各種セラミックス
よりなる丸棒（直径１０ｍｍ、長さ１０ｍｍ）を用意
し、接合面となる片側端面に蒸着法により厚さ１μｍの
Ａｌ膜５を成膜した。アルミニウム合金部材３として表
１に示すＪＩＳに規格する材料よりなる丸棒（直径１０
ｍｍ、長さ５０ｍｍ）を用意した。また非熱処理型アル
ミニウム合金からなる中間部材４として表１に示すＪＩ
Ｓに規格する材料よりなる円板（直径１０ｍｍ、厚さ
０．５ｍｍ）を準備した。ろう材６として、５８％Ｚｎ
−３０％Ａｌ−１０％Ｃｕー２％Ｓｉの合金箔（直径１
０ｍｍ、厚さ０．０５ｍｍ）を準備し、これらを図２に
示す順番に重ね合せ、図示しない治具にセットした。こ
れらを加熱炉中にセットして窒素中にて、４７０℃で２
時間保持してろう付を行なった。得られた接合体１に溶
体化処理を行なった後、時効処理を行なった。溶体化処
理は、表１に記載の各温度に１時間保持したのち直ちに
図５に示す様にアルミニウム合金部材３の丸棒部分のみ
を水焼入れすることにより行なった。--Experimental Example 1-- As a ceramic member 2, a round bar (diameter 10 mm, length 10 mm) made of various ceramics shown in Table 1 was prepared, and an Al film having a thickness of 1 μm was formed on one end surface to be a joint surface by vapor deposition. 5 was deposited. As the aluminum alloy member 3, a round bar (diameter 10
mm, length 50 mm). The JI shown in Table 1 as the intermediate member 4 made of a non-heat treatment type aluminum alloy.
A disk (diameter 10 mm, thickness 0.5 mm) made of a material specified by S was prepared. As the brazing material 6, 58% Zn
-30% Al-10% Cu-2% Si alloy foil (diameter 1
0 mm, thickness 0.05 mm) were prepared, these were piled up in the order shown in FIG. 2 and set on a jig (not shown). Set these in a heating furnace and place in nitrogen at 470 ° C for 2
Brazing was performed while holding the time. The obtained joined body 1 was subjected to solution treatment and then subjected to aging treatment. The solution treatment was carried out by holding each temperature shown in Table 1 for 1 hour and then immediately water quenching only the round bar portion of the aluminum alloy member 3 as shown in FIG.
【０００１１】なお比較例として、中間部材を用いずに
直接両部材を接合したもの（Ｎｏ.１４）についても同
様に溶体化処理後に時効処理を行なった。時効処理を完
了した接合体の少なくとも接合部の外周を直径９ｍｍと
なるまで円筒研削し、図６に示す様にアルミニウム合金
部材３側をクランプしてセラミックス部材２に荷重をか
ける片持曲げ試験にて接合強度を評価した。また、評価
終了後にアルミニウム合金部材３の丸棒を切断してビッ
カース硬度を測定した。結果を表１に示す。As a comparative example, the one in which both members were directly joined without using the intermediate member (No. 14) was similarly subjected to the solution treatment and then the aging treatment. In a cantilever bending test in which at least the outer periphery of the joined portion of the joined body that has been aged is cylindrically ground to a diameter of 9 mm, and the aluminum alloy member 3 side is clamped to apply a load to the ceramic member 2 as shown in FIG. And the bonding strength was evaluated. After the evaluation, the round bar of the aluminum alloy member 3 was cut to measure the Vickers hardness. The results are shown in Table 1.
【００１２】[0012]
【表１】 [Table 1]
【００１３】本発明の実施例の接合体は、いずれもセラ
ミックス部材にクラックや部材同士の剥離の発生がなく
良好な接合強度を有したが、中間部材を用いない比較例
の接合体（Ｎｏ.１３、Ｎｏ.１４）は溶体化処理の際に
セラミックス部材にクラックが発生していた。結果から
分かるように中間部材が軟質で厚さが厚くなることによ
り、接合体の応力緩和が十分に行われていた。よって、
接合強度が上昇し、軟質である中間部材が変形するに至
ったと考えられる。中間部材が厚い分、変形の度合いが
大きかった（Ｎｏ.５、Ｎｏ.７、Ｎｏ.１２）。The joints of the examples of the present invention all had good joint strength without cracks in the ceramic members or separation of the members from each other, but the joints of the comparative example (No. No. 13, No. 14) had cracks in the ceramic member during the solution treatment. As can be seen from the results, the intermediate member was soft and had a large thickness, whereby the stress of the bonded body was sufficiently relaxed. Therefore,
It is considered that the joint strength increased and the soft intermediate member was deformed. The thicker the intermediate member, the greater the degree of deformation (No. 5, No. 7, No. 12).
【００１４】ー実験例２ー セラミックス部材２として表２に示す各種セラミックス
よりなる丸棒（直径１０ｍｍ、長さ１０ｍｍ）を用意
し、接合面となる片側端面に蒸着法により厚さ１μｍの
Ａｌ膜５を成膜した。アルミニウム合金部材３として表
２に示すＪＩＳに規格する材料よりなる丸棒（直径１０
ｍｍ、長さ５０ｍｍ）を用意した。また非熱処理型アル
ミニウム合金からなる中間部材４、中間部材８として表
２に示すＪＩＳに規格する材料よりなる円板（直径１０
ｍｍ、厚さ０．５ｍｍ）を準備した。ろう材６として、
５８％Ｚｎ−３０％Ａｌ−１０％Ｃｕー２％Ｓｉの合金
箔（直径１０ｍｍ、厚さ０．０５ｍｍ）を準備し、これ
らを図３に示す順番に重ね合せ、図示しない治具にセッ
トした。これらを加熱炉中にセットして窒素中にて、４
７０℃で２時間保持してろう付を行なった。得られた接
合体１に溶体化処理を行なった後、時効処理を行なっ
た。溶体化処理は、表２に記載の各温度に１時間保持し
たのち直ちに図５に示す様にアルミニウム合金部材３の
丸棒部分のみを水焼入れすることにより行なった。時効
処理を完了した接合体の少なくとも接合部の外周を直径
９ｍｍとなるまで円筒研削し、図６に示す様にアルミニ
ウム合金部材３側をクランプしてセラミックス部材２に
荷重をかける片持曲げ試験にて接合強度を評価した。ま
た、評価終了後にアルミニウム合金部材３の丸棒を切断
してビッカース硬度を測定した。結果を表２に示す。--Experimental Example 2-- As a ceramic member 2, a round bar (diameter 10 mm, length 10 mm) made of various ceramics shown in Table 2 was prepared, and an Al film having a thickness of 1 μm was formed on one end surface to be a joint surface by vapor deposition. 5 was deposited. As the aluminum alloy member 3, a round bar (diameter 10
mm, length 50 mm). Further, as the intermediate member 4 and the intermediate member 8 made of the non-heat treatment type aluminum alloy, a disk (diameter 10
mm, thickness 0.5 mm) was prepared. As brazing material 6,
An alloy foil of 58% Zn-30% Al-10% Cu-2% Si (diameter 10 mm, thickness 0.05 mm) was prepared, these were stacked in the order shown in FIG. 3, and set on a jig (not shown). . Set these in a heating furnace and place in nitrogen for 4
Brazing was performed by holding at 70 ° C. for 2 hours. The obtained joined body 1 was subjected to solution treatment and then subjected to aging treatment. The solution treatment was performed by holding each temperature shown in Table 2 for 1 hour and then immediately water quenching only the round bar portion of the aluminum alloy member 3 as shown in FIG. In a cantilever bending test in which at least the outer periphery of the joined portion of the joined body that has been aged is cylindrically ground to a diameter of 9 mm, and the aluminum alloy member 3 side is clamped to apply a load to the ceramic member 2 as shown in FIG. And the bonding strength was evaluated. After the evaluation, the round bar of the aluminum alloy member 3 was cut to measure the Vickers hardness. Table 2 shows the results.
【００１５】[0015]
【表２】 [Table 2]
【００１６】本発明の実施例の接合体は、いずれもセラ
ミックス部材にクラックや部材同士の剥離の発生がなく
良好な接合強度を有した。結果から分かるように中間部
材が軟質で厚さが厚くなることにより、接合体の応力緩
和が十分に行われていた。よって、接合強度が上昇し、
軟質である中間部材が変形するに至ったと考えられる。
中間部材が厚い分、変形の度合いが大きかった（Ｎｏ.
２２）。また、実施例１に比べ、中間部材の数に起因
し、全体的に接合強度が高かった。All of the joined bodies of the examples of the present invention had good joining strength without cracks in the ceramic members or peeling of the members from each other. As can be seen from the results, the intermediate member was soft and had a large thickness, whereby the stress of the bonded body was sufficiently relaxed. Therefore, the bonding strength increases,
It is considered that the soft intermediate member has been deformed.
The thicker the intermediate member, the greater the degree of deformation (No.
22). In addition, due to the number of intermediate members, the bonding strength was higher overall as compared with Example 1.
【００１７】−実験例３− セラミックス部材２として表３に示すセラミックスより
なる丸棒（直径１０ｍｍ、長さ１０ｍｍ）を用意し、接
合面となる片側端面に蒸着法により厚さ１μｍのＡｌ膜
５を成膜した。アルミニウム合金部材３として表３に示
すＪＩＳに規格する材料よりなる丸棒（直径１０ｍｍ、
長さ５０ｍｍ）を用意した。また非熱処理型アルミニウ
ム合金からなる中間部材４、中間部材８、中間部材１０
として表３に示すＪＩＳに規格する材料よりなる円板
（直径１０ｍｍ、厚さ０．５ｍｍ）を準備した。ろう材
６として、５８％Ｚｎ−３０％Ａｌ−１０％Ｃｕー２％
Ｓｉの合金箔（直径１０ｍｍ、厚さ０．０５ｍｍ）を準
備し、これらを図４に示す順番に重ね合せ、図示しない
治具にセットした。これらを加熱炉中にセットして窒素
中にて、４７０℃で２時間保持してろう付を行なった。
得られた接合体１に溶体化処理を行なった後、時効処理
を行なった。溶体化処理は、表３に記載の各温度に１時
間保持したのち直ちに図５に示す様にアルミニウム合金
部材３の丸棒部分のみを水焼入れすることにより行なっ
た。時効処理を完了した接合体の少なくとも接合部の外
周を直径９ｍｍとなるまで円筒研削し、図６に示す様に
アルミニウム合金部材３側をクランプしてセラミックス
部材２に荷重をかける片持曲げ試験にて接合強度を評価
した。また、評価終了後にアルミニウム合金部材３の丸
棒を切断してビッカース硬度を測定した。結果を表３に
示す。Experimental Example 3 As the ceramic member 2, a round bar (diameter 10 mm, length 10 mm) made of ceramics shown in Table 3 was prepared, and an Al film 5 having a thickness of 1 μm was formed on one end face to be a joint surface by vapor deposition. Was deposited. As the aluminum alloy member 3, a round bar (diameter 10 mm, made of a material specified in JIS shown in Table 3
(Length 50 mm). Further, the intermediate member 4, the intermediate member 8 and the intermediate member 10 made of a non-heat treatment type aluminum alloy.
A disk (diameter: 10 mm, thickness: 0.5 mm) made of a JIS standard material shown in Table 3 was prepared. As the brazing material 6, 58% Zn-30% Al-10% Cu-2%
Alloy foils of Si (diameter 10 mm, thickness 0.05 mm) were prepared, these were stacked in the order shown in FIG. 4, and set on a jig (not shown). These were set in a heating furnace and held in nitrogen at 470 ° C. for 2 hours for brazing.
The obtained joined body 1 was subjected to solution treatment and then subjected to aging treatment. The solution treatment was carried out by holding each temperature shown in Table 3 for 1 hour and then immediately water quenching only the round bar portion of the aluminum alloy member 3 as shown in FIG. In a cantilever bending test in which at least the outer periphery of the joined portion of the joined body that has been aged is cylindrically ground to a diameter of 9 mm, and the aluminum alloy member 3 side is clamped to apply a load to the ceramic member 2 as shown in FIG. And the bonding strength was evaluated. After the evaluation, the round bar of the aluminum alloy member 3 was cut to measure the Vickers hardness. The results are shown in Table 3.
【００１８】[0018]
【表３】 [Table 3]
【００１９】本発明の実施例の接合体は、いずれもセラ
ミックス部材にクラックや部材同士の剥離の発生がなく
良好な接合強度を有した。結果から分かるように中間部
材が軟質で厚さが厚くなることにより、接合体の応力緩
和が十分に行われていた。よって、接合強度が上昇し、
軟質である中間部材が変形するに至ったと考えられる。
中間部材が厚い分、変形の度合いが大きかった（Ｎｏ.
２３）。また、実施例１及び実施例２に比べ、中間部材
の数に起因し、全体的に接合強度が高かった。All of the bonded bodies of the examples of the present invention had good bonding strength without cracks in the ceramic members or peeling of the members from each other. As can be seen from the results, the intermediate member was soft and had a large thickness, whereby the stress of the bonded body was sufficiently relaxed. Therefore, the bonding strength increases,
It is considered that the soft intermediate member has been deformed.
The thicker the intermediate member, the greater the degree of deformation (No.
23). Moreover, compared with Examples 1 and 2, due to the number of intermediate members, the overall bonding strength was high.
【００２０】[0020]
【発明の効果】本発明による構造の接合体とすることに
より、高強度なアルミニウム合金部材とセラミックス部
材とが強固に接合された接合体を得ることができる。EFFECTS OF THE INVENTION By using the joined body having the structure according to the present invention, a joined body in which a high-strength aluminum alloy member and a ceramic member are firmly joined can be obtained.
【図１】実験例１の本発明のアルミニウム合金部材とセ
ラミックス部材との接合体の斜視図である。FIG. 1 is a perspective view of a joined body of an aluminum alloy member of the present invention and a ceramic member of Experimental Example 1.
【図２】実験例１の本発明のアルミニウム合金部材とセ
ラミックス部材との接合体の両部材を接合する直前の状
態を示す正面図である。FIG. 2 is a front view showing a state immediately before joining both members of the joined body of the aluminum alloy member of the present invention and the ceramic member of Experimental Example 1.
【図３】実験例２の本発明のアルミニウム合金部材とセ
ラミックス部材との接合体の両部材を接合する直前の状
態を示す正面図である。FIG. 3 is a front view showing a state immediately before joining both members of a joined body of an aluminum alloy member of the present invention and a ceramic member of Experimental Example 2.
【図４】実験例３の本発明のアルミニウム合金部材とセ
ラミックス部材との接合体の両部材を接合する直前の状
態を示す正面図である。FIG. 4 is a front view showing a state immediately before joining both members of a joined body of an aluminum alloy member of the present invention and a ceramic member of Experimental Example 3.
【図５】溶体化処理の方法を示す正面図である。FIG. 5 is a front view showing a solution treatment method.
【図６】接合強度を評価する方法を示す正面図である。FIG. 6 is a front view showing a method for evaluating bonding strength.
１ ・・・ アルミニウム合金部材とセラミックス部材
との接合体 ２ ・・・ セラミックス部材 ３ ・・・ アルミニウム合金部材 ４ ・・・ 中間部材 ５ ・・・ Ａｌ膜 ６ ・・・ ろう材 ７ ・・・ 水 ８ ・・・ 中間部材 １０・・・ 中間部材1 ... Joined body of aluminum alloy member and ceramics member 2 ... Ceramics member 3 ... Aluminum alloy member 4 ... Intermediate member 5 ... Al film 6 ... Brazing material 7 ... Water 8 ... Intermediate member 10 ... Intermediate member
Claims (7)
ミックス部材とが非熱処理型アルミニウム合金からなる
中間部材を介して接合されていることを特徴とするアル
ミニウム合金部材とセラミックス部材との接合体。1. A joined body of an aluminum alloy member and a ceramic member, wherein the age hardening type aluminum alloy member and the ceramic member are joined via an intermediate member made of a non-heat treatment type aluminum alloy.
ミックス部材とが非熱処理型アルミニウム合金からなる
中間部材を２以上介して接合されていることを特徴とす
るアルミニウム合金部材とセラミックス部材との接合
体。2. A joined body of an aluminum alloy member and a ceramic member, wherein the age hardening type aluminum alloy member and the ceramic member are joined via two or more intermediate members made of a non-heat treatment type aluminum alloy.
−Ｍｇ系合金であることを特徴とする請求項１又は２に
記載のアルミニウム合金部材とセラミックス部材との接
合体。3. The non-heat treatment type aluminum alloy is Al
A joined body of the aluminum alloy member and the ceramic member according to claim 1 or 2, which is a Mg-based alloy.
を９９重量％以上含有することを特徴とする請求項１又
は２に記載のアルミニウム合金部材とセラミックス部材
との接合体。4. The non-heat treatment type aluminum alloy is Al
99% by weight or more is contained, The joined body of the aluminum alloy member and the ceramic member of Claim 1 or 2 characterized by the above-mentioned.
ｍであることを特徴とする請求項１〜４のいずれかに記
載のアルミニウム合金部材とセラミックス部材との接合
体。5. The intermediate member has a thickness of 0.1 to 2.0 m.
The bonded body of the aluminum alloy member and the ceramic member according to any one of claims 1 to 4, wherein m is m.
ｍであることを特徴とする請求項１〜４のいずれかに記
載のアルミニウム合金部材とセラミックス部材との接合
体。6. The intermediate member has a thickness of 0.1 to 1.0 m.
The bonded body of the aluminum alloy member and the ceramic member according to any one of claims 1 to 4, wherein m is m.
がＨｖ１００以上であることを特徴とする請求項１〜６
のいずれかに記載のアルミニウム合金部材とセラミック
ス部材との接合体。7. The age hardening type aluminum alloy member has a hardness of Hv100 or more.
A joined body of the aluminum alloy member and the ceramic member according to any one of 1.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP11015296A JPH0940476A (en) | 1995-05-22 | 1996-04-04 | Joined body of aluminum alloy member and ceramic member |
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP14817895 | 1995-05-22 | ||
| JP7-148178 | 1995-05-22 | ||
| JP11015296A JPH0940476A (en) | 1995-05-22 | 1996-04-04 | Joined body of aluminum alloy member and ceramic member |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH0940476A true JPH0940476A (en) | 1997-02-10 |
Family
ID=26449829
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP11015296A Pending JPH0940476A (en) | 1995-05-22 | 1996-04-04 | Joined body of aluminum alloy member and ceramic member |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0940476A (en) |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2007111056A1 (en) * | 2006-03-28 | 2007-10-04 | Ngk Insulators, Ltd. | Honeycomb structure and method for producing same |
| JP2016052979A (en) * | 2014-09-04 | 2016-04-14 | 国立研究開発法人産業技術総合研究所 | Method for bonding ceramic member and aluminum member |
| JP2017094390A (en) * | 2015-10-19 | 2017-06-01 | 株式会社神戸製鋼所 | Aluminum structural member |
| WO2017213258A1 (en) * | 2016-06-09 | 2017-12-14 | 国立研究開発法人産業技術総合研究所 | Method for producing conjugate, and conjugate |
| EP3584492A4 (en) * | 2017-02-15 | 2021-03-17 | Bogachek, Oleg Evgenievich | Vessel made of thermally non-hardenable aluminum alloy and method for the production thereof |
-
1996
- 1996-04-04 JP JP11015296A patent/JPH0940476A/en active Pending
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2007111056A1 (en) * | 2006-03-28 | 2007-10-04 | Ngk Insulators, Ltd. | Honeycomb structure and method for producing same |
| US7947103B2 (en) | 2006-03-28 | 2011-05-24 | MGK Insulators, Ltd. | Honeycomb structure and method for producing same |
| JP5103377B2 (en) * | 2006-03-28 | 2012-12-19 | 日本碍子株式会社 | Honeycomb structure and manufacturing method thereof |
| JP2016052979A (en) * | 2014-09-04 | 2016-04-14 | 国立研究開発法人産業技術総合研究所 | Method for bonding ceramic member and aluminum member |
| JP2017094390A (en) * | 2015-10-19 | 2017-06-01 | 株式会社神戸製鋼所 | Aluminum structural member |
| WO2017213258A1 (en) * | 2016-06-09 | 2017-12-14 | 国立研究開発法人産業技術総合研究所 | Method for producing conjugate, and conjugate |
| JPWO2017213258A1 (en) * | 2016-06-09 | 2019-03-07 | 国立研究開発法人産業技術総合研究所 | Manufacturing method of joined body and joined body |
| EP3584492A4 (en) * | 2017-02-15 | 2021-03-17 | Bogachek, Oleg Evgenievich | Vessel made of thermally non-hardenable aluminum alloy and method for the production thereof |
| US11644151B2 (en) | 2017-02-15 | 2023-05-09 | Oleg Evgenievich BOGACHEK | Vessel made of thermally non-hardenable aluminum alloy and method for the production thereof |
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