JP2004225061A - Aluminum alloy clad tube material excellent in corrosion resistance and heat exchanger incorporating the clad tube material - Google Patents
Aluminum alloy clad tube material excellent in corrosion resistance and heat exchanger incorporating the clad tube material Download PDFInfo
- Publication number
- JP2004225061A JP2004225061A JP2003010556A JP2003010556A JP2004225061A JP 2004225061 A JP2004225061 A JP 2004225061A JP 2003010556 A JP2003010556 A JP 2003010556A JP 2003010556 A JP2003010556 A JP 2003010556A JP 2004225061 A JP2004225061 A JP 2004225061A
- Authority
- JP
- Japan
- Prior art keywords
- aluminum alloy
- sacrificial anode
- clad tube
- less
- content
- 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.)
- Granted
Links
Landscapes
- Prevention Of Electric Corrosion (AREA)
- Laminated Bodies (AREA)
Abstract
【課題】内面にブレージングシートからなるフィンがろう付け接合されて冷媒通路となり、外面側にもフィンがろう付けされ、大気からの結露水や融雪剤などに曝される場合に好適に使用できる熱交換器用部材として、強度、ろう付け性および耐食性に優れたアルミニウム合金クラッドチューブ材、および当該クラッドチューブ材を組付けたコンデンサ、エバポレータのような熱交換器を提供する。
【解決手段】芯材用アルミニウム合金に犠牲陽極材用アルミニウム合金をクラッドしてなる厚さ３００μｍ以下のクラッドチューブ材であり、内面側が芯材、外面側が犠牲陽極材となるよう成形されていることを特徴とする。
【選択図】 なしA fin made of a brazing sheet is brazed and joined to an inner surface to form a refrigerant passage, and a fin is brazed to an outer surface to be used preferably when exposed to dew condensation water or a snow melting agent from the atmosphere. As a member for an exchanger, an aluminum alloy clad tube material excellent in strength, brazing property and corrosion resistance, and a heat exchanger such as a condenser or an evaporator to which the clad tube material is assembled are provided.
The clad tube is formed by cladding an aluminum alloy for a core material with an aluminum alloy for a sacrificial anode material and having a thickness of 300 μm or less. The clad tube is formed so that the inner surface is a core material and the outer surface is a sacrificial anode material. It is characterized by.
[Selection diagram] None
Description
【０００１】
【発明の属する技術分野】
本発明は、耐食性に優れたアルミニウム合金クラッドチューブ材、とくに自動車用エバポレータ、コンデンサのように、外面の耐食性が問題となる熱交換器部材として好適に使用される耐食性に優れたアルミニウム合金クラッドチューブ材および該クラッドチューブ材を組付けた熱交換器に関する。
【０００２】
【従来の技術】
従来、自動車用のラジエータ、ヒータコアのように、冷却水が内面側を循環している熱交換器のチューブ材として、Ａｌ−Ｍｎ系合金などを芯材とし、芯材にＡｌ−Ｚｎ系合金などの犠牲陽極材をクラッドし、芯材を外面側、犠牲陽極材を内面側となるよう成形したアルミニウム合金クラッド材、あるいはこのクラッド材の外面の芯材にさらにＡｌ−Ｓｉ系合金ろう材をクラッドしたアルミニウム合金クラッド材が使用されている（特許文献１参照）。
【０００３】
上記従来のアルミニウム合金クラッド材において、チューブ内面側の犠牲陽極材は冷却水に起因する腐食を防止するためのものであり、外面側のＡｌ−Ｓｉ系合金ろう材は、チューブ外面にアウターフィンをろう付け接合するためのものである。アウターフィンは犠牲陽極効果を発揮して芯材を防食する。
【０００４】
また、アルミニウム合金芯材の両面にＡｌ−Ｓｉ系合金ろう材を有し、芯材とろう材との間に犠牲陽極材をクラッドしてなる４層クラッド材も提案されている（特許文献２参照）。この４層クラッド材は、例えばドロンカップ型エバポレータの部材として使用される。
【０００５】
ドロンカップ型エバポレータは、プレス成形した４層クラッド材よりなるコアプレートとコルゲート成形したフィンとを積層し、コアプレートのろう材を介してコアプレートとフィンとを接合し、コアプレートの間に冷媒通路を形成してなるものである。
【０００６】
エバポレータの使用環境は、凝縮水など伝導度の低い水溶液に曝されるため、フィンによる防食効果が発揮され難く、従ってクラッド材自身の耐食性が重要となり、高寿命価を図るために芯材とろう材との間に犠牲陽極材を介在させている。
【０００７】
しかしながら、ろう材が存在することにより犠牲陽極材の消耗速度が早まり、腐食が促進されるという問題がある。この問題を解消するために、最近、両面にＡｌ−Ｓｉ系合金ろう材を有するクラッド材を用いることなく、チューブ材の内外面にブレージングフィンを装着してろう付け接合する構造の新規なエバポレータが提案されている。
【０００８】
【特許文献１】
特開平１１−２９３３７２号公報（請求項１、請求項２）
【特許文献２】
特開２００２−１２９３５号公報（請求項６、図２）
【０００９】
【発明が解決しようとする課題】
本発明の目的は、両面にＡｌ−Ｓｉ系合金ろう材を有するクラッド材を用いることのない上記の新規な構造のエバポレータや、コンデンサなど、内面にフィンがろう付け接合されて冷媒通路となり、外面側にもフィンがろう付けされ、大気からの結露水や融雪剤などに曝される場合に好適に使用できる熱交換器用部材として、強度、ろう付け性および耐食性に優れたアルミニウム合金クラッドチューブ材および当該クラッドチューブ材を組付けた熱交換器を提供するものである。
【００１０】
【課題を解決するための手段】
上記の目的を達成するための本発明の請求項１による耐食性に優れたアルミニウム合金クラッドチューブ材は、芯材用アルミニウム合金に犠牲陽極材用アルミニウム合金をクラッドしてなる厚さ３００μｍ以下のクラッドチューブ材であり、内面側が芯材、外面側が犠牲陽極材となるよう成形されていることを特徴とする。
【００１１】
請求項２によるアルミニウム合金クラッドチューブ材は、請求項１において、犠牲陽極材用アルミニウム合金が、Ｚｎ２〜６％、Ｉｎ０．０１〜０．１％、Ｓｎ０．０１〜０．１％のうちの１種以上を含有し、残部Ａｌおよび不純物からなり、Ｆｅ含有量を０．５％以下、Ｍｇ含有量を０．５％以下に制限したことを特徴とする。
【００１２】
請求項３によるアルミニウム合金クラッドチューブは、請求項２において、犠牲陽極材用アルミニウム合金が、さらにＭｎ０．１〜０．８％を含有し、Ｓｉ含有量を０．２％未満に制限したことを特徴とする。
【００１３】
請求項４によるアルミニウム合金クラッドチューブ材は、請求項２において、犠牲陽極材用アルミニウム合金が、さらにＳｉ０．２〜１．０％を含有し、Ｍｎ含有量を０．１％未満に制限したことを特徴とする。
【００１４】
請求項５によるアルミニウム合金クラッドチューブ材は、請求項１において、犠牲陽極材用アルミニウム合金が、Ｚｎ３〜６％、Ｉｎ０．０２〜０．０６％、Ｓｎ０．０３〜０．０８％のうちの１種以上を含有し、さらにＭｎ０．１〜０．８％を含有し、残部Ａｌおよび不純物からなり、Ｆｅ含有量を０．５％以下、Ｍｇ含有量を０．５％以下、Ｓｉ含有量を０．２％未満に制限したことを特徴とする。
【００１５】
請求項６によるアルミニウム合金クラッドチューブ材は、請求項１において、犠牲陽極材用アルミニウム合金が、Ｚｎ３〜６％、Ｉｎ０．０２〜０．０６％、Ｓｎ０．０３〜０．０８％のうちの１種以上を含有し、さらにＳｉ０．２〜１．０％を含有し、残部Ａｌおよび不純物からなり、Ｆｅ含有量を０．５％以下、Ｍｇ含有量を０．５％以下、Ｍｎ含有量を０．１％未満に制限したことを特徴とする。
【００１６】
請求項７によるアルミニウム合金クラッドチューブ材は、請求項２〜６のいずれかにおいて、犠牲陽極材用アルミニウム合金が、さらにＣｒ０．０５〜０．２５％、Ｚｒ０．０５〜０．２５％の１種または２種を含有することを特徴とする。
【００１７】
請求項８によるアルミニウム合金クラッドチューブ材は、請求項１〜７のいずれかにおいて、芯材用アルミニウム合金が、Ｓｉ０．２〜１％、Ｃｕ０．１〜０．８％、Ｍｎ０．６〜２％、Ｔｉ０．１〜０．３％を含有し、残部Ａｌおよび不純物からなり、Ｍｇ含有量を０．５％以下に制限したことを特徴とする。
【００１８】
請求項９によるアルミニウム合金クラッドチューブ材は、請求項１〜８のいずれかにおいて、犠牲陽極材が厚さ１５μｍ以上、クラッド率４０％以下でクラッドされていることを特徴とする。
【００１９】
請求項１０によるアルミニウム合金クラッドクラッドチューブ材は、請求項１〜９のいずれかにおいて、芯材が厚さ３０μｍ以上でクラッドされていることを特徴とする。
【００２０】
請求項１１によるアルミニウム合金クラッドチューブ材は、請求項１〜１０のいずれかにおいて、アルミニウム合金クラッドチューブ材がＨ調質材であることを特徴とする。
【００２１】
また、本発明による熱交換器は、請求項１〜１１のいずれかに記載のクラッドチューブ材の内部にブレージングからなるインナーフィンを装着、ろう付け加熱時にろう材を生成させるペーストを塗布したベアフィンをインナーフィンとして装着、またはクラッドチューブ材の内面に前記ペーストを塗布しベアフィンをインナーフィンとして装着、ろう付け接合してなり、ろう付け後、芯材と犠牲陽極材の界面から犠牲陽極材側に１５μｍの部位におけるＣｕ濃度が、ろう付け加熱前の段階での芯材の平均Ｃｕ濃度の１／２以下であることを特徴とする。
【００２２】
【発明の実施の形態】
本発明のアルミニウム合金クラッドチューブ材の構成の意義およびその限定理由について説明する。
（犠牲陽極材の組成）
Ｚｎは、クラッドチューブ材に犠牲陽極効果を与えるよう機能する。Ｚｎの好ましい含有量は２〜６％の範囲であり、２％未満ではその効果が十分でなく、６％を越えると自己腐食による消耗が激しくなる。Ｚｎのさらに好ましい含有範囲は２〜５％である。
【００２３】
Ｉｎは、クラッドチューブ材に犠牲陽極効果を与えるよう機能する。Ｉｎの好ましい含有量は０．０１〜０．１％の範囲であり、０．０１％未満ではその効果が十分でなく、０．１％を越えると自己腐食による消耗が激しくなる。Ｉｎのさらに好ましい含有範囲は０．０２〜０．０６％である。
【００２４】
Ｓｎは、クラッドチューブ材に犠牲陽極効果を与えるよう機能する。Ｓｎの好ましい含有量は０．０１〜０．１％の範囲であり、０．０１％未満ではその効果が十分でなく、０．１％を越えると自己腐食による消耗が激しくなる。Ｓｎのさらに好ましい含有範囲は０．０３〜０．０８％である。
【００２５】
Ｆｅは、０．５％以下に制限するのが好ましく、０．５％を越えると自己腐食速度が大きくなる。０．１％以下に制限するのがさらに好ましいが、例えば０．０１％未満まで低減するには高純度地金を使用しなければならずコスト高となるから、コスト的には０．０１％以上とすることが望ましい。
【００２６】
Ｍｇは、フッ化物系フラックスを使用するろう付けにおいて、フッ化物と反応してろう付け性を害するので、０．５％以下に制限することが好ましい。
【００２７】
Ｍｎは、強度を高めるよう機能する。Ｍｎの好ましい含有量は０．１〜０．８％の範囲であり、０．１％未満ではその効果が小さく、幅方向のクラッド率が不均一となる。０．８％を越えると自己腐食が激しくなる。Ｍｎを０．１〜０．８％の範囲で含有する場合は、Ｓｉ量を０．２％未満に限定することが好ましく、０．２％以上含有すると、Ｍｎと化合物を形成し自己腐食量が多くなる。さらに好ましくはＳｉを０．１％以下に限定するが、Ｓｉ量を例えば０．０１％未満にまで低減するには高純度地金を使用しなければならずコスト高となるから、コスト的には０．０１％以上とすることが望ましい。
【００２８】
また、Ｍｎを０．１〜０．８％含有させた場合におけるＺｎ、ＩｎおよびＳｎは、それらのうちの１種以上をそれぞれ３〜６％、０．０２〜０．０６％および０．０３〜０．０８％の範囲で含有させるのが好ましい。
【００２９】
Ｓｉは、強度を高めるよう機能する。Ｓｉの好ましい含有量は０．２〜１．０％の範囲であり、０．２％未満では幅方向のクラッド率が不均一となる。１．０％を越えると自己腐食が激しくなる。Ｓｉを０．２〜１．０％の範囲で含有する場合は、Ｍｎ量を０．１％未満に限定することが好ましく、０．１％以上含有すると、Ｓｉと化合物を形成し自己腐食量が多くなる。好ましくは０．０５％以下に限定する。
【００３０】
また、Ｓｉを０．２〜１．０％含有させた場合におけるＺｎ、ＩｎおよびＳｎは、それらのうちの１種以上をそれぞれ３〜６％、０．０２〜０．０６％および０．０３〜０．０８％の範囲で含有させるのが好ましい。
【００３１】
Ｃｒは、ろう付け加熱時に結晶粒を粗大化してろう付け性を改善する。Ｃｒの好ましい含有量は０．０５〜０．２５％の範囲であり、０．０５％未満ではその効果が小さく、０．２５％を越えると巨大晶出物が生成し、巨大晶出物周辺部でのクラッド率を不安定にする。
【００３２】
Ｚｒは、ろう付け加熱時に結晶粒を粗大化してろう付け性を改善する。Ｚｒの好ましい含有量は０．０５〜０．２５％の範囲であり、０．０５％未満ではその効果が小さく、０．２５％を越えると巨大晶出物が生成し、巨大晶出物周辺部でのクラッド率を不安定にする。
【００３３】
（芯材の組成）
Ｓｉは、強度を向上させるよう機能する。Ｓｉの好ましい含有量は０．２〜１％の範囲であり、０．２％未満ではその効果が十分でなく、１％を越えて含有すると融点が低下し、ろう付け接合部に溶融が生じ易くなる。Ｓｉのさらに好ましい含有範囲は０．５〜０．９％である。
【００３４】
Ｃｕは、芯材の電位を貴にするよう作用する。Ｃｕの好ましい含有量は０．１〜０．８％の範囲であり、０．１％未満ではその効果が十分でなく、０．８％を越えると融点が低下し、ろう付け接合部に溶融が生じ易くなる。Ｃｕのさらに好ましい含有範囲は０．２％を越え０．８％以下である。
【００３５】
Ｍｎは、強度を高めるよう機能する。Ｍｎの好ましい含有量は０．６〜２％の範囲であり、０．６％未満ではその効果が小さく、２％を越えると強度が大きくなり圧延が困難となる。Ｍｎのさらに好ましい含有範囲は１．５％を越え２％以下である。
【００３６】
Ｍｇは０．５％以下に制限することが必要であり、０．５％を越えて含有すると、フッ化物系フラックスを使用するろう付けにおいて、Ｍｇがフラックスと反応し、ろう付け性を害する。
【００３７】
Ｔｉは、層状に分布して腐食形態を層状の全面腐食型とし、耐食性を向上させる。Ｔｉの好ましい含有量は０．１〜０．３％の範囲であり、０．１％未満ではその効果が小さく、０．３％を越えると巨大化合物が生成し、巨大化合物周辺部におけるクラッド率を不均一にする。
【００３８】
（クラッドチューブ材の厚さ）
本発明のアルミニウム合金管材は、芯材用アルミニウム合金に犠牲陽極材用アルミニウム合金をクラッドしてなる厚さ３００μｍ以下のクラッドチューブ材であり、熱交換器の軽量化を達成し得る薄肉化されたクラッドチューブ材を得るものである。好ましい厚さは４５〜３００μｍであり、４５μｍ未満では十分な耐食性が得難くなる。
【００３９】
（犠牲陽極材の厚さ）
本発明のクラッドチューブ材における犠牲陽極材のクラッド厚は１５μｍ以上で、クラッド率は４０％以下が好ましい。クラッド厚が１５μｍ未満では犠牲陽極効果が小さく十分な耐食性が得難く、クラッド率が４０％を越えるとクラッドが困難となる。
【００４０】
（芯材の厚さ）
本発明のクラッドチューブ材における芯材の厚さは３０μｍ以上とすることが好ましい。３０μｍ未満では、芯材と犠牲陽極材との電位差を確保することが困難となって犠牲陽極効果は発揮できず貫通腐食が生じ易くなる。
【００４１】
（調質）
本発明のクラッドチューブ材はＨ調質材、とくに冷間加工材、クラッドチューブ材に成形する前のクラッド材はＨ１４材などの冷間圧延材であることが望ましい。例えば、Ｏ材では、ろう付け時に、ろうが芯材中に浸透してろう付け性を低下させ、また、ろう付け時に犠牲陽極材にエロージョンが生じ易くなる。
【００４２】
本発明による熱交換器は、クラッドチューブ材の内部にブレージングからなるインナーフィンを装着、ろう付け加熱時にろう材を生成させるペーストを塗布したベアフィンをインナーフィンとして装着、またはクラッドチューブ材の内面に前記ペーストを塗布しベアフィンをインナーフィンとして装着、ろう付け接合してなるもので、ろう付け後、芯材と犠牲陽極材の界面から犠牲陽極材側に１５μｍの部位におけるＣｕ濃度が、ろう付け加熱前の段階での芯材の平均Ｃｕ濃度の１／２以下とすることにより、犠牲陽極材と芯材との電位差が十分に確保され、犠牲陽極効果が顕著に発揮される。
【００４３】
本発明のアルミニウム合金クラッドチューブ材は、芯材と犠牲陽極材を構成するアルミニウム合金を、例えば半連続鋳造により造塊し、必要に応じて均質化理した後、それぞれ所定の厚さまで熱間圧延し、ついで、各材料を組合わせ、常法に従って熱間圧延し、必要に応じて中間焼鈍を行いながら、所定厚さまで冷間圧延することによってクラッド材とし、これを曲成することにより製造される。
【００４４】
本発明のアルミニウム合金クラッドチューブ材を、自動車用エバポレータ、コンデンサなどに適用する場合には、例えば、クラッド材を曲成してチューブ形状としたクラッドチューブ材の内部にブレージングシートからなるインナーフィンが装着、ろう付け加熱時にろう材を生成させるペーストを塗布したベアフィンをインナーフィンとして装着、またはクラッドチューブ材の内面に前記ペーストを塗布しベアフィンをインナーフィンとして装着、ろう付け接合し、外面側にもアウターフィンがろう付けされる。内部は冷媒通路となり、外面は大気からの結露水や融雪剤などに曝されるが、犠牲陽極材の存在により芯材を保護する。
【００４５】
【実施例】
以下、本発明の実施例を比較例と対比して説明する。なお、これらの実施例は、本発明の一実施態様を示すものであり、本発明はこれらに限定されるものではない。
【００４６】
実施例１
表１に示す組成を有する犠牲陽極材用アルミニウム合金および表２に示す組成を有する芯材用アルミニウム合金を半連続鋳造により造塊し、犠牲陽極用アルミニウム合金の鋳塊については２００〜６００℃で１〜２０時間、芯材用アルミニウム合金の鋳塊については４００〜６００℃で５〜２０時間均質化処理した後、面削した。ついで、表３に示す組み合わせで、犠牲陽極材／芯材となるように重ね合わせ、３００〜５５０℃で熱間圧延を行い、さらに、必要に応じて２００〜５００℃での中間焼鈍を介して冷間圧延を行いクラッド材（クラッドチューブ材）とした。得られたクラッド材における犠牲陽極材の厚さとクラッド率、芯材の厚さとクラッド率およびクラッド材全体厚さを表３に示す。
【００４７】
上記クラッド材を試験材として、下記の方法で耐食性、ろう付け性、クラッド性および強度を評価した。結果を表４に示す。
耐食性：犠牲陽極材側に、Ｃｌ− ５００ｐｐｍ、ＳＯ４ ２− ２０００ｐｐｍを含む５０℃の腐食液（ｐＨ３）を６時間噴霧し、５０℃の温度で６時間乾燥するサイクルを行い、貫通腐食が生じるまでに２０００時間以上を要するものは合格（○）、２０００時間未満で貫通腐食が生じるものは不合格（×）とする。また、下記のろう付け性評価時に、芯材と犠牲陽極材の界面近傍のＣｕ濃度（ろう付け加熱時、界面から犠牲陽極材側へ芯材中のＣｕが拡散する）を測定した。
【００４８】
ろう付け性：Ａｌ−Ｍｎ系合金芯材、Ａｌ−１０％Ｓｉ合金ろう材からなるブレージングシートをコルゲート加工してフィン材とし、これを試験材の犠牲陽極材面にアウターフィンとして組合わせ、また試験材の芯材面にインナーフィンとして組合わせ、フッ化物系フラックスを塗布して６００℃の温度でろう付け接合し、接合率が９８％以上のものを合格（○）、９８％未満のものを不合格（×）とする。
【００４９】
クラッド性：冷間圧延コイルとして得られるクラッド材の幅方向において、クラッド率が設定値の±５％を外れる部分がコイル両端から８ｃｍを越え１５ｍｍ以下の場合は○、８ｃｍ以下の場合は◎とする。
強度：クラッド材と同じ工程で作製した芯材から引張試験片を採取して引張試験を行い、引張強さが１２０ＭＰａ以上のものを合格（○）、１２０ＭＰａ未満のものを不合格（×）とする。実際の使用環境においては、犠牲陽極材は腐食により消耗して、芯材のみが残存し芯材のみで熱交換器の強度を維持する場合が多い。
【００５０】
【表１】
【表２】
【表３】
【表４】
表４にみられるように、本発明に従う試験材Ｎｏ．１〜２０はいずれも、耐食性、ろう付け性。クラッド性に優れ、１３０ＭＰａ以上の優れた強度を有している。また、圧延加工性も良好であった。
【００５５】
比較例１
表５に示す組成を有する犠牲陽極材用アルミニウム合金および表６に示す組成を有する芯材用アルミニウム合金を半連続鋳造により造塊し、犠牲陽極用アルミニウム合金の鋳塊については２００〜６００℃で１〜２０時間、芯材用アルミニウム合金の鋳塊については４００〜６００℃で５〜２０時間均質化処理した後、面削した。ついで、表３に示す組み合わせで、犠牲陽極材／芯材となるように重ね合わせ、３００〜５５０℃で熱間圧延を行い、さらに、必要に応じて２００〜５００℃での中間焼鈍を介して冷間圧延を行いクラッド材（クラッドチューブ材）とした。得られたクラッド材における犠牲陽極材の厚さとクラッド率、芯材の厚さとクラッド率およびクラッド材全体厚さを表７〜８に示す。なお、表５〜８において、本発明の条件を外れたものには下線を付した。
【００５６】
上記クラッド材を試験材として、実施例１と同じ方法で耐食性、ろう付け性、クラッド性および強度を評価した。結果を表９〜１０に示す。なお、試験材Ｎｏ．２５以外はＨ１４材に調質され、試験材Ｎｏ．２５はＯ材（焼鈍材）に調質された。
【００５７】
【表５】
【表６】
【表７】
【表８】
【表９】
【表１０】
表９〜１０に示すように、試験材Ｎｏ．２１は犠牲陽極材のＳｉが多く単体Ｓｉが晶出するため、犠牲陽極材の消耗速度が早くなり耐食性が劣る。また、犠牲陽極材とアウターフィンのろう付け接合部において犠牲陽極材に溶融が生じ、ろう付け性が害される。試験材Ｎｏ．２２は、犠牲陽極材のＭｎとＳｉの含有量の組合わせが適切でないため、Ａｌ−Ｍｎ−Ｓｉ系の化合物が生成して犠牲陽極材の消耗速度が大きくなり、耐食性が劣る。試験材Ｎｏ．２３は犠牲陽極材のＦｅ量が多いため、Ａｌ−Ｆｅ系化合物が生成して犠牲陽極材の消耗速度が大きくなり、耐食性が劣る。また、犠牲陽極材の結晶粒径が微細となるため、ろう付け時にろうが犠牲陽極材の結晶粒界に浸透し、ろう付け性を害する。
【００６４】
試験材Ｎｏ．２４は犠牲陽極材のＭｎ量が多いため、Ａｌ−Ｍｎ系化合物が生成して犠牲陽極材の消耗速度が大きくなり、耐食性が劣る。また、Ｃｒ、Ｚｒの添加が少ないため、その効果も認められない。試験材Ｎｏ．２５は、犠牲陽極材のＭｎとＳｉの含有量の組合わせが適切でないため、Ａｌ−Ｍｎ−Ｓｉ系の化合物が生成して犠牲陽極材の消耗速度が大きくなり、耐食性が劣る。また、Ｏ材に調質されているため、ろう付け時、芯材中にろうが浸透してろう付け不良が生じた。試験材Ｎｏ．２６は犠牲陽極材のＭｇ量が多いため、Ｍｇがフッ化物系フラックスと反応して、ろう付け性が害される。
【００６５】
試験材Ｎｏ．２７は犠牲陽極材のＣｒ量が多いため、Ａｌ−Ｃｒ系の巨大晶出物が生成し、この晶出物周辺部においてクラッド率が不均一となった。試験材Ｎｏ．２８は犠牲陽極材のＺｒ量が多いため、Ａｌ−Ｚｒ系の巨大晶出物が生成し、この晶出物周辺部においてクラッド率が不均一となった。試験材Ｎｏ．２９は犠牲陽極材のＺｎ量が多いため、犠牲陽極材の消耗が顕著となり耐食性が劣る。
【００６６】
試験材Ｎｏ．３０は犠牲陽極材のＺｎ、Ｉｎ、Ｓｎ量が少なく犠牲陽極材の犠牲陽極効果が十分に発揮されないため耐食性が劣り、早期に貫通腐食が生じた。試験材Ｎｏ．３１は犠牲陽極材のＩｎ量が多いため、犠牲陽極材の消耗速度が大きく耐食性が劣る。試験材Ｎｏ．３２はＳｎ量が多いため、犠牲陽極材の消耗速度が大きく耐食性が劣る。
【００６７】
試験材Ｎｏ．３３は芯材のＳｉ量が多いため、ろう付け時、ろう付け接合部に溶融が生じ、ろう付け性が害される。試験材Ｎｏ．３４は芯材のＳｉ量が少ないため強度が不十分となった。試験材Ｎｏ．３５は芯材のＣｕ量が多いため、ろう付け時、ろう付け接合部に溶融が生じ、ろう付け性が害される。試験材Ｎｏ．３６は芯材のＣｕ量が少なく芯材と犠牲陽極材との電位差が十分に確保できないため、犠牲陽極材の犠牲陽極効果が不十分となり耐食性が劣る。
【００６８】
試験材Ｎｏ．３７は芯材のＭｎ量が多いため、芯材が硬くなり熱間圧延が困難となってクラッド材の製造ができなかった。試験材Ｎｏ．３８は芯材のＭｎ量が少ないため強度が不十分となった。試験材Ｎｏ．３９は芯材のＭｇ量が多いため、Ｍｇがフッ化物系フラックスと反応して、ろう付け性が害される。
【００６９】
試験材Ｎｏ．４０は芯材のＴｉ量が多いため、Ａｌ−Ｔｉ系の巨大晶出物が生成し、この晶出物周辺部においてクラッド率が不均一となった。試験材Ｎｏ．４１は芯材のＴｉ量が少ないため、芯材が層状腐食形態を示さず、早期に貫通腐食が生じた。試験材Ｎｏ．４２は犠牲陽極材のクラッド率が高いため、熱間圧延時に犠牲陽極材と芯材とが接合せずクラッド材が製造できなかった。
【００７０】
試験材Ｎｏ．４３は犠牲陽極材の厚さが小さいため、犠牲陽極材の犠牲陽極効果が十分に発揮されず耐食性に劣る。試験材Ｎｏ．４４はクラッド材の全体厚さが小さく、犠牲陽極材の厚さも小さいため、犠牲陽極材の犠牲陽極効果が十分に発揮されず耐食性に劣る。試験材Ｎｏ．４５はろう付け加熱時の保持時間を長くしたもので、芯材と犠牲陽極材との界面のＣｕ濃度が高くなり、Ｃｕの犠牲陽極材への拡散が生じるため、犠牲陽極材の犠牲陽極効果が不十分となり早期に貫通腐食が生じた。
【００７１】
【発明の効果】
本発明によれば、内面にブレージングシートからなるフィンがろう付け接合されて冷媒通路となり、外面側にもフィンがろう付けされ、大気からの結露水や融雪剤などに曝される場合に好適に使用できる熱交換器用部材、とくに自動車用熱交換器部材として、強度、ろう付け性および耐食性に優れたアルミニウム合金クラッドチューブ材、および当該クラッドチューブ材を組付けたコンデンサ、エバポレータのような熱交換器が提供される。[0001]
TECHNICAL FIELD OF THE INVENTION
The present invention provides an aluminum alloy clad tube material having excellent corrosion resistance, particularly an aluminum alloy clad tube material having excellent corrosion resistance which is suitably used as a heat exchanger member having a problem of corrosion resistance on the outer surface, such as an evaporator for automobiles and capacitors. And a heat exchanger to which the clad tube material is attached.
[0002]
[Prior art]
Conventionally, as a tube material of a heat exchanger in which cooling water circulates on the inner surface side, such as a radiator or a heater core for an automobile, an Al-Mn alloy is used as a core material, and an Al-Zn alloy is used as a core material. An aluminum alloy clad material in which the sacrificial anode material is clad and the core material is formed on the outer surface side and the sacrificial anode material is formed on the inner surface side, or an Al-Si alloy brazing material is further clad on the outer core material of the clad material. An aluminum alloy clad material is used (see Patent Document 1).
[0003]
In the above conventional aluminum alloy clad material, the sacrificial anode material on the inner surface side of the tube is for preventing corrosion caused by cooling water, and the Al-Si alloy brazing material on the outer surface side has outer fins on the outer surface of the tube. It is for brazing. The outer fin exerts a sacrificial anode effect to protect the core material from corrosion.
[0004]
In addition, a four-layer clad material in which an Al-Si alloy brazing material is provided on both surfaces of an aluminum alloy core material and a sacrificial anode material is clad between the core material and the brazing material has been proposed (Patent Document 2). reference). This four-layer clad material is used, for example, as a member of a drone cup type evaporator.
[0005]
The drone cup type evaporator laminates a press-formed core plate made of a four-layer clad material and a corrugated fin, joins the core plate and the fins through the brazing material of the core plate, and forms a coolant between the core plates. A passage is formed.
[0006]
The environment in which the evaporator is used is exposed to an aqueous solution with low conductivity, such as condensed water, so that the fins are unlikely to exhibit the anticorrosion effect.Therefore, the corrosion resistance of the clad material itself is important, and the core material will be used to achieve a long service life. A sacrificial anode material is interposed between the material.
[0007]
However, there is a problem that the presence of the brazing material speeds up the consumption of the sacrificial anode material and promotes corrosion. In order to solve this problem, recently, a new evaporator having a structure in which brazing fins are mounted on the inner and outer surfaces of a tube material and brazed and joined without using a clad material having an Al-Si alloy brazing material on both surfaces has been developed. Proposed.
[0008]
[Patent Document 1]
JP-A-11-293372 (Claims 1 and 2)
[Patent Document 2]
JP-A-2002-12935 (Claim 6, FIG. 2)
[0009]
[Problems to be solved by the invention]
An object of the present invention is to provide an evaporator having the above-described novel structure without using a clad material having an Al-Si alloy brazing material on both surfaces, a condenser, and the like, and fins are brazed to the inner surface to form a refrigerant passage, and the outer surface is formed. Fins are also brazed on the side, and as a heat exchanger member that can be suitably used when exposed to dew condensation water or snow melting agent from the atmosphere, aluminum alloy clad tube material excellent in strength, brazing property and corrosion resistance and A heat exchanger provided with the clad tube material is provided.
[0010]
[Means for Solving the Problems]
The aluminum alloy clad tube material excellent in corrosion resistance according to claim 1 of the present invention for attaining the above object is a clad tube having a thickness of 300 μm or less formed by cladding an aluminum alloy for a core material with an aluminum alloy for a sacrificial anode material. Characterized in that the inner surface side is formed as a core material and the outer surface side is formed as a sacrificial anode material.
[0011]
The aluminum alloy clad tube material according to claim 2 is the aluminum alloy for a sacrificial anode material according to claim 1, wherein the aluminum alloy for sacrificial anode material is one of Zn2 to 6%, In 0.01 to 0.1%, and Sn 0.01 to 0.1%. It is characterized by containing at least one species, the balance being Al and impurities, the Fe content is limited to 0.5% or less, and the Mg content is limited to 0.5% or less.
[0012]
The aluminum alloy clad tube according to claim 3 is characterized in that, in claim 2, the aluminum alloy for a sacrificial anode material further contains Mn 0.1 to 0.8%, and the Si content is limited to less than 0.2%. Features.
[0013]
In the aluminum alloy clad tube material according to claim 4, in claim 2, the aluminum alloy for a sacrificial anode material further contains 0.2 to 1.0% of Si, and the Mn content is limited to less than 0.1%. It is characterized by.
[0014]
The aluminum alloy clad tube according to claim 5 is the aluminum alloy for a sacrificial anode material according to claim 1, wherein the aluminum alloy for sacrificial anode material is one of Zn3 to 6%, In 0.02 to 0.06%, and Sn 0.03 to 0.08%. At least 0.1% to 0.8% of Mn, the balance being Al and impurities, the Fe content is 0.5% or less, the Mg content is 0.5% or less, and the Si content is It is characterized by being limited to less than 0.2%.
[0015]
The aluminum alloy clad tube material according to claim 6 is the aluminum alloy for a sacrificial anode material according to claim 1, wherein the aluminum alloy for sacrificial anode material is one of Zn3 to 6%, In 0.02 to 0.06%, and Sn 0.03 to 0.08%. Containing at least 0.1% of Si, further containing 0.2 to 1.0% of Si, the balance being Al and impurities, the Fe content is 0.5% or less, the Mg content is 0.5% or less, and the Mn content is It is characterized by being limited to less than 0.1%.
[0016]
An aluminum alloy clad tube material according to claim 7 is the aluminum alloy for a sacrificial anode material according to any one of claims 2 to 6, wherein the aluminum alloy for a sacrificial anode material is further one of Cr 0.05 to 0.25% and Zr 0.05 to 0.25%. Or, it is characterized by containing two types.
[0017]
The aluminum alloy clad tube material according to claim 8 is the aluminum alloy for core material according to any one of claims 1 to 7, wherein the aluminum alloy for the core material is Si 0.2 to 1%, Cu 0.1 to 0.8%, and Mn 0.6 to 2%. , Ti of 0.1 to 0.3%, the balance being Al and impurities, and the Mg content is limited to 0.5% or less.
[0018]
The aluminum alloy clad tube material according to claim 9 is characterized in that, in any one of claims 1 to 8, the sacrificial anode material is clad at a thickness of 15 μm or more and a cladding ratio of 40% or less.
[0019]
An aluminum alloy clad tube material according to claim 10 is characterized in that, in any one of claims 1 to 9, the core material is clad with a thickness of 30 µm or more.
[0020]
The aluminum alloy clad tube material according to claim 11 is characterized in that, in any one of claims 1 to 10, the aluminum alloy clad tube material is an H heat treatment material.
[0021]
In addition, the heat exchanger according to the present invention is provided with an inner fin made of brazing inside the clad tube material according to any one of claims 1 to 11, and a bare fin coated with a paste that generates a brazing material during brazing heating. The paste is applied to the inner surface of the cladding tube material, and the bare fin is mounted as the inner fin and brazed and joined. After brazing, 15 μm from the interface between the core material and the sacrificial anode material to the sacrificial anode material side. Is characterized in that the Cu concentration in the portion is not more than 1/2 of the average Cu concentration of the core material before the brazing heating.
[0022]
BEST MODE FOR CARRYING OUT THE INVENTION
The significance of the structure of the aluminum alloy clad tube material of the present invention and the reason for the limitation will be described.
(Composition of sacrificial anode material)
Zn functions to give a sacrificial anode effect to the cladding tube material. The preferred content of Zn is in the range of 2 to 6%. If the content is less than 2%, the effect is not sufficient, and if it exceeds 6%, the consumption due to self-corrosion becomes severe. The more preferable content range of Zn is 2 to 5%.
[0023]
In functions to provide a sacrificial anode effect to the cladding tube material. The preferred content of In is in the range of 0.01 to 0.1%. If the content is less than 0.01%, the effect is not sufficient, and if it exceeds 0.1%, the consumption due to self-corrosion becomes severe. The more preferable content range of In is 0.02 to 0.06%.
[0024]
Sn functions to provide a sacrificial anode effect to the cladding tube material. The preferred content of Sn is in the range of 0.01 to 0.1%. If the content is less than 0.01%, the effect is not sufficient, and if it exceeds 0.1%, the consumption due to self-corrosion becomes severe. The more preferable content range of Sn is 0.03 to 0.08%.
[0025]
Fe is preferably limited to 0.5% or less, and if it exceeds 0.5%, the self-corrosion rate increases. More preferably, the content is limited to 0.1% or less. However, for example, in order to reduce the content to less than 0.01%, a high-purity ingot must be used, which increases the cost. It is desirable to make the above.
[0026]
In brazing using a fluoride-based flux, Mg reacts with fluoride and impairs the brazing properties. Therefore, it is preferable to limit Mg to 0.5% or less.
[0027]
Mn functions to increase the strength. The preferred content of Mn is in the range of 0.1 to 0.8%. If the content is less than 0.1%, the effect is small, and the cladding ratio in the width direction becomes non-uniform. If it exceeds 0.8%, self-corrosion becomes severe. When Mn is contained in the range of 0.1 to 0.8%, it is preferable to limit the amount of Si to less than 0.2%. Increase. More preferably, the content of Si is limited to 0.1% or less. However, in order to reduce the amount of Si to less than 0.01%, for example, a high-purity metal has to be used, which increases the cost. Is desirably 0.01% or more.
[0028]
Zn, In and Sn when Mn is contained at 0.1 to 0.8% contain at least one of them at 3 to 6%, 0.02 to 0.06% and 0.03%, respectively. It is preferable to contain it in the range of -0.08%.
[0029]
Si functions to increase the strength. The preferred content of Si is in the range of 0.2 to 1.0%, and if it is less than 0.2%, the cladding ratio in the width direction becomes non-uniform. If it exceeds 1.0%, self-corrosion becomes severe. When Si is contained in the range of 0.2 to 1.0%, the Mn content is preferably limited to less than 0.1%, and when 0.1% or more is contained, a compound is formed with Si and the amount of self-corrosion is increased. Increase. Preferably, it is limited to 0.05% or less.
[0030]
Zn, In and Sn when Si is contained in an amount of 0.2 to 1.0% contain at least one of them at 3 to 6%, 0.02 to 0.06% and 0.03%, respectively. It is preferable to contain it in the range of -0.08%.
[0031]
Cr improves the brazing properties by coarsening the crystal grains during brazing heating. The preferable content of Cr is in the range of 0.05 to 0.25%. When the content is less than 0.05%, the effect is small. When the content exceeds 0.25%, a giant crystal is formed, and the vicinity of the giant crystal is generated. Destabilizes the cladding rate in the part.
[0032]
Zr increases the crystal grains during brazing and improves brazing properties. The preferable content of Zr is in the range of 0.05 to 0.25%. When the content is less than 0.05%, the effect is small, and when it exceeds 0.25%, a giant crystal is formed. Destabilizes the cladding rate in the part.
[0033]
(Composition of core material)
Si functions to improve the strength. The preferable content of Si is in the range of 0.2 to 1%. If the content is less than 0.2%, the effect is not sufficient. If the content is more than 1%, the melting point is lowered and the brazing joint is melted. It will be easier. The more preferable content range of Si is 0.5 to 0.9%.
[0034]
Cu acts to make the potential of the core material noble. The preferred content of Cu is in the range of 0.1 to 0.8%. If the content is less than 0.1%, the effect is not sufficient. Tends to occur. The more preferable content range of Cu is more than 0.2% and 0.8% or less.
[0035]
Mn functions to increase the strength. The preferred content of Mn is in the range of 0.6 to 2%. If the content is less than 0.6%, the effect is small, and if it exceeds 2%, the strength is increased and the rolling becomes difficult. The more preferable content range of Mn is more than 1.5% and 2% or less.
[0036]
Mg must be limited to 0.5% or less, and if it exceeds 0.5%, in brazing using a fluoride-based flux, Mg reacts with the flux and impairs brazing properties.
[0037]
Ti is distributed in a layered manner, and the corrosion form is a layered general corrosion type, thereby improving the corrosion resistance. The preferable content of Ti is in the range of 0.1 to 0.3%. When the content is less than 0.1%, the effect is small. When the content is more than 0.3%, a giant compound is generated, and the cladding ratio around the giant compound is increased. Is uneven.
[0038]
(Thickness of clad tube material)
The aluminum alloy tube material of the present invention is a clad tube material having a thickness of 300 μm or less obtained by cladding an aluminum alloy for a core material with an aluminum alloy for a sacrificial anode material, and has a reduced thickness capable of achieving a light weight heat exchanger. A clad tube material is obtained. The preferred thickness is 45 to 300 μm, and if it is less than 45 μm, it is difficult to obtain sufficient corrosion resistance.
[0039]
(Thickness of sacrificial anode material)
The clad thickness of the sacrificial anode material in the clad tube material of the present invention is preferably 15 μm or more, and the clad ratio is preferably 40% or less. If the clad thickness is less than 15 μm, the sacrificial anode effect is small and sufficient corrosion resistance cannot be obtained, and if the clad ratio exceeds 40%, the cladding becomes difficult.
[0040]
(Thickness of core material)
The thickness of the core material in the clad tube material of the present invention is preferably 30 μm or more. If it is less than 30 μm, it is difficult to secure a potential difference between the core material and the sacrificial anode material, so that the sacrificial anode effect cannot be exerted and penetration corrosion tends to occur.
[0041]
(refining)
It is preferable that the clad tube material of the present invention is an H-tempered material, particularly a cold-worked material, and the clad material before being formed into a clad tube material is a cold-rolled material such as H14 material. For example, in the case of the O material, at the time of brazing, the brazing material penetrates into the core material to reduce the brazing property, and erosion tends to occur in the sacrificial anode material at the time of brazing.
[0042]
The heat exchanger according to the present invention mounts an inner fin made of brazing inside the clad tube material, mounts a bare fin coated with a paste that generates a brazing material at the time of brazing heating as an inner fin, or the inner surface of the clad tube material. The paste is applied, and bare fins are attached as inner fins and brazed. The brazing is performed, and after the brazing, the Cu concentration at a portion of 15 μm from the interface between the core material and the sacrificial anode material to the sacrificial anode material side is determined before brazing. By setting the average Cu concentration of the core material to 段 階 or less at the stage, the potential difference between the sacrificial anode material and the core material is sufficiently ensured, and the sacrificial anode effect is remarkably exhibited.
[0043]
The aluminum alloy clad tube material of the present invention is obtained by ingoting the aluminum alloy constituting the core material and the sacrificial anode material by, for example, semi-continuous casting, homogenizing if necessary, and then hot rolling to a predetermined thickness. Then, the respective materials are combined, hot-rolled according to a conventional method, and, while performing intermediate annealing as necessary, cold-rolled to a predetermined thickness to form a clad material, which is manufactured by bending. You.
[0044]
When the aluminum alloy clad tube material of the present invention is applied to an automotive evaporator, a capacitor, or the like, for example, an inner fin made of a brazing sheet is mounted inside a clad tube material obtained by bending a clad material into a tube shape. A bare fin coated with a paste that generates a brazing material at the time of brazing heating is attached as an inner fin, or the paste is applied to the inner surface of a clad tube material, and the bare fin is attached as an inner fin, brazed and joined, and the outer surface is also outer. Fins are brazed. The inside is a refrigerant passage, and the outside is exposed to dew condensation water and snow melting agent from the atmosphere, but the core material is protected by the presence of the sacrificial anode material.
[0045]
【Example】
Hereinafter, examples of the present invention will be described in comparison with comparative examples. These examples show one embodiment of the present invention, and the present invention is not limited to these.
[0046]
Example 1
An aluminum alloy for a sacrificial anode material having a composition shown in Table 1 and an aluminum alloy for a core material having a composition shown in Table 2 were ingot-formed by semi-continuous casting. The ingot of the aluminum alloy for the core material was homogenized at 400 to 600 ° C. for 5 to 20 hours for 1 to 20 hours, and then the surface was cut. Then, in the combinations shown in Table 3, they are superimposed so as to be a sacrificial anode material / core material, hot-rolled at 300 to 550 ° C, and, if necessary, through intermediate annealing at 200 to 500 ° C. Cold rolling was performed to obtain a clad material (clad tube material). Table 3 shows the thickness and cladding ratio of the sacrificial anode material, the thickness and the cladding ratio of the core material, and the total thickness of the clad material in the obtained clad material.
[0047]
Using the above clad material as a test material, the corrosion resistance, brazing property, clad property and strength were evaluated by the following methods. Table 4 shows the results.
Corrosion: the sacrificial anode material side, Cl - 500 ppm, and 6 hours spray corrosion solution (pH 3) of 50 ° C. containing SO 4 2- 2000ppm, performs cycle to dry for six hours at a temperature of 50 ° C., occurs through corrosion A sample that requires 2,000 hours or more to pass is rated as acceptable (（), and one that causes penetration corrosion in less than 2,000 hours is rated as unacceptable (x). Further, at the time of the brazing property evaluation described below, the Cu concentration near the interface between the core material and the sacrificial anode material (Cu in the core material diffuses from the interface to the sacrificial anode material side during the brazing heating) was measured.
[0048]
Brazing ability: A brazing sheet composed of an Al-Mn alloy core material and an Al-10% Si alloy brazing material is corrugated to form a fin material, which is combined with a sacrificial anode material surface of a test material as an outer fin. Combined as inner fins on the core material surface of the test material, apply fluoride flux and braze at 600 ° C. Pass rate of 98% or more is acceptable (o), less than 98% Is rejected (x).
[0049]
Clad properties: In the width direction of the clad material obtained as a cold-rolled coil, a portion where the clad ratio deviates from ± 5% of the set value exceeds 8 cm from both ends of the coil and is 15 mm or less, and ○ is 8 cm or less. I do.
Strength: Tensile test specimens were taken from the core material prepared in the same process as the clad material and subjected to a tensile test, and those with a tensile strength of 120 MPa or more passed (合格), and those with less than 120 MPa failed (×). I do. In an actual use environment, the sacrificial anode material is often consumed by corrosion, leaving only the core material, and maintaining the strength of the heat exchanger only with the core material.
[0050]
[Table 1]
[Table 2]
[Table 3]
[Table 4]
As can be seen in Table 4, test material No. 1 to 20 are all corrosion resistance and brazing properties. It has excellent cladding properties and excellent strength of 130 MPa or more. The rolling workability was also good.
[0055]
Comparative Example 1
An aluminum alloy for a sacrificial anode material having a composition shown in Table 5 and an aluminum alloy for a core material having a composition shown in Table 6 were ingot-formed by semi-continuous casting. The ingot of the aluminum alloy for the core material was homogenized at 400 to 600 ° C. for 5 to 20 hours for 1 to 20 hours, and then the surface was cut. Then, in the combinations shown in Table 3, they are superimposed so as to be a sacrificial anode material / core material, hot-rolled at 300 to 550 ° C, and, if necessary, through intermediate annealing at 200 to 500 ° C. Cold rolling was performed to obtain a clad material (clad tube material). Tables 7 and 8 show the thickness and cladding ratio of the sacrificial anode material, the thickness and cladding ratio of the core material, and the overall thickness of the clad material in the obtained clad material. In Tables 5 to 8, the values outside the conditions of the present invention are underlined.
[0056]
Using the above-mentioned clad material as a test material, corrosion resistance, brazing property, clad property and strength were evaluated in the same manner as in Example 1. The results are shown in Tables 9 to 10. The test material No. The test material No. 25 was tempered to H14 material. No. 25 was tempered to an O material (annealed material).
[0057]
[Table 5]
[Table 6]
[Table 7]
[Table 8]
[Table 9]
[Table 10]
As shown in Tables 9 to 10, the test material No. In No. 21, since the amount of Si in the sacrificial anode material is large and single Si is crystallized, the consumption speed of the sacrificial anode material is increased, and the corrosion resistance is poor. In addition, the sacrificial anode material is melted at the brazed joint between the sacrificial anode material and the outer fin, and the brazing property is impaired. Test material No. In No. 22, since the combination of the Mn and Si contents of the sacrificial anode material is not appropriate, an Al-Mn-Si-based compound is generated, the consumption rate of the sacrificial anode material is increased, and the corrosion resistance is poor. Test material No. In No. 23, since the amount of Fe in the sacrificial anode material is large, an Al—Fe-based compound is generated, the consumption rate of the sacrificial anode material is increased, and the corrosion resistance is poor. Further, since the crystal grain size of the sacrificial anode material becomes fine, the brazing material penetrates into the crystal grain boundaries of the sacrificial anode material during brazing, impairing the brazing property.
[0064]
Test material No. In No. 24, since the amount of Mn in the sacrificial anode material is large, an Al—Mn-based compound is generated, the consumption rate of the sacrificial anode material is increased, and the corrosion resistance is poor. Further, since the addition of Cr and Zr is small, the effect is not recognized. Test material No. In No. 25, since the combination of the Mn and Si contents of the sacrificial anode material is not appropriate, an Al-Mn-Si-based compound is generated, the consumption rate of the sacrificial anode material is increased, and the corrosion resistance is poor. In addition, since the material was tempered with the O material, the brazing material penetrated into the core material during brazing, resulting in poor brazing. Test material No. In No. 26, since the amount of Mg in the sacrificial anode material is large, Mg reacts with the fluoride-based flux to impair brazing properties.
[0065]
Test material No. In No. 27, since the amount of Cr in the sacrificial anode material was large, an Al-Cr-based giant crystallized product was formed, and the cladding ratio became nonuniform in the periphery of the crystallized material. Test material No. In No. 28, since the amount of Zr in the sacrificial anode material was large, an Al-Zr-based giant crystallized product was generated, and the cladding ratio became nonuniform in the periphery of the crystallized material. Test material No. In No. 29, since the amount of Zn in the sacrificial anode material is large, consumption of the sacrificial anode material is remarkable and corrosion resistance is poor.
[0066]
Test material No. In No. 30, the amount of Zn, In, and Sn of the sacrificial anode material was small and the sacrificial anode effect of the sacrificial anode material was not sufficiently exhibited, so that the corrosion resistance was poor, and penetration corrosion occurred early. Test material No. 31 has a large In content of the sacrificial anode material, so the consumption rate of the sacrificial anode material is large and the corrosion resistance is poor. Test material No. No. 32 has a large amount of Sn, so the consumption rate of the sacrificial anode material is large and the corrosion resistance is inferior.
[0067]
Test material No. In the case of No. 33, since the amount of Si in the core material is large, melting occurs at the brazing joint at the time of brazing, and the brazing property is impaired. Test material No. In No. 34, the strength was insufficient because the amount of Si in the core material was small. Test material No. In the case of No. 35, since the amount of Cu in the core material is large, at the time of brazing, melting occurs at the brazed joint, and the brazing property is impaired. Test material No. In No. 36, since the Cu content of the core material is small and the potential difference between the core material and the sacrificial anode material cannot be sufficiently ensured, the sacrificial anode effect of the sacrificial anode material is insufficient and the corrosion resistance is poor.
[0068]
Test material No. In No. 37, since the core material had a large Mn content, the core material became hard and hot rolling became difficult, so that the clad material could not be manufactured. Test material No. No. 38 had insufficient strength because the Mn content of the core material was small. Test material No. Since 39 has a large amount of Mg in the core material, Mg reacts with the fluoride-based flux, and the brazing property is impaired.
[0069]
Test material No. In No. 40, since the amount of Ti in the core material was large, an Al-Ti-based giant crystallized product was generated, and the cladding ratio became non-uniform in the periphery of the crystallized material. Test material No. In No. 41, since the amount of Ti in the core material was small, the core material did not show the form of layered corrosion, and penetration corrosion occurred early. Test material No. In No. 42, the cladding ratio of the sacrificial anode material was high, so that the sacrificial anode material and the core material were not joined at the time of hot rolling, so that a clad material could not be produced.
[0070]
Test material No. 43 has a small thickness of the sacrificial anode material, so that the sacrificial anode effect of the sacrificial anode material is not sufficiently exhibited, and the corrosion resistance is poor. Test material No. In reference numeral 44, since the entire thickness of the clad material is small and the thickness of the sacrificial anode material is also small, the sacrificial anode effect of the sacrificial anode material is not sufficiently exhibited and the corrosion resistance is poor. Test material No. Numeral 45 indicates a longer holding time during brazing heating. The Cu concentration at the interface between the core material and the sacrificial anode material increases, and Cu diffuses into the sacrificial anode material. Was insufficient and penetration corrosion occurred early.
[0071]
【The invention's effect】
According to the present invention, a fin made of a brazing sheet is brazed to the inner surface to form a refrigerant passage, and the fin is brazed also to the outer surface, which is suitably used when exposed to dew condensation water or a snow melting agent from the atmosphere. Aluminum alloy clad tube material excellent in strength, brazeability and corrosion resistance, and heat exchangers such as capacitors and evaporators with the clad tube material as heat exchanger members that can be used, especially heat exchanger members for automobiles Is provided.
Claims (12)
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2003010556A JP4190295B2 (en) | 2003-01-20 | 2003-01-20 | Aluminum alloy clad tube material excellent in corrosion resistance and heat exchanger assembled with the clad tube material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2003010556A JP4190295B2 (en) | 2003-01-20 | 2003-01-20 | Aluminum alloy clad tube material excellent in corrosion resistance and heat exchanger assembled with the clad tube material |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2004225061A true JP2004225061A (en) | 2004-08-12 |
| JP4190295B2 JP4190295B2 (en) | 2008-12-03 |
Family
ID=32899713
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2003010556A Expired - Lifetime JP4190295B2 (en) | 2003-01-20 | 2003-01-20 | Aluminum alloy clad tube material excellent in corrosion resistance and heat exchanger assembled with the clad tube material |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP4190295B2 (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2009074138A (en) * | 2007-09-21 | 2009-04-09 | Kobe Steel Ltd | Composite material of aluminum alloy, and heat exchanger |
| JP2009074137A (en) * | 2007-09-21 | 2009-04-09 | Kobe Steel Ltd | Composite material of aluminum alloy, and heat exchanger |
| EP2243589A1 (en) * | 2009-04-21 | 2010-10-27 | Sumitomo Light Metal Industries, Ltd. | Aluminum alloy clad sheet for heat exchangers and method of producing the same |
| US9012033B2 (en) | 2009-04-21 | 2015-04-21 | Denso Corporation | Aluminum alloy clad sheet for heat exchangers |
| US10788275B2 (en) | 2014-11-21 | 2020-09-29 | Denso Corporation | Aluminum alloy cladding material for heat exchanger |
| US11015234B2 (en) | 2014-11-21 | 2021-05-25 | Uacj Corporation | Aluminum alloy cladding material for heat exchanger |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109807556A (en) * | 2019-01-21 | 2019-05-28 | 大力神铝业股份有限公司 | A kind of preparation method of sedan-chair vehicle-used warm air blower fin material |
-
2003
- 2003-01-20 JP JP2003010556A patent/JP4190295B2/en not_active Expired - Lifetime
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2009074138A (en) * | 2007-09-21 | 2009-04-09 | Kobe Steel Ltd | Composite material of aluminum alloy, and heat exchanger |
| JP2009074137A (en) * | 2007-09-21 | 2009-04-09 | Kobe Steel Ltd | Composite material of aluminum alloy, and heat exchanger |
| EP2243589A1 (en) * | 2009-04-21 | 2010-10-27 | Sumitomo Light Metal Industries, Ltd. | Aluminum alloy clad sheet for heat exchangers and method of producing the same |
| US9012033B2 (en) | 2009-04-21 | 2015-04-21 | Denso Corporation | Aluminum alloy clad sheet for heat exchangers |
| US10788275B2 (en) | 2014-11-21 | 2020-09-29 | Denso Corporation | Aluminum alloy cladding material for heat exchanger |
| US11015234B2 (en) | 2014-11-21 | 2021-05-25 | Uacj Corporation | Aluminum alloy cladding material for heat exchanger |
Also Published As
| Publication number | Publication date |
|---|---|
| JP4190295B2 (en) | 2008-12-03 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP5079198B2 (en) | Aluminum brazing alloy | |
| JP2002059291A (en) | Aluminum alloy brazing sheet for heat exchanger | |
| JP2011202285A (en) | Brazing sheet | |
| CN107428128A (en) | Multilayer Aluminum Brazing Sheet Material | |
| JP3772017B2 (en) | High strength and high corrosion resistance aluminum alloy clad material for heat exchanger | |
| JP4190295B2 (en) | Aluminum alloy clad tube material excellent in corrosion resistance and heat exchanger assembled with the clad tube material | |
| JP3360026B2 (en) | Brazing method of aluminum alloy brazing sheet for heat exchanger | |
| JPH10249580A (en) | Manufacturing method of Al alloy brazing filler metal and heat exchanger made of Al alloy | |
| JP2000167688A (en) | Aluminum alloy clad material for heat exchangers with excellent brazing and corrosion resistance | |
| JP3326106B2 (en) | Aluminum alloy clad material for heat exchanger with excellent strength and corrosion resistance | |
| JP4263160B2 (en) | Aluminum alloy clad material and heat exchanger tube and heat exchanger using the same | |
| JP2007131872A (en) | Aluminum alloy clad material for heat exchanger | |
| JP2006037135A (en) | High corrosion resistance aluminum clad material for heat exchanger | |
| JP3222768B2 (en) | Aluminum alloy clad material excellent in brazing property and method for producing the same | |
| JPH1088265A (en) | Aluminum alloy fin material for heat exchanger with excellent strength after brazing and sacrificial anode effect | |
| JP2004225062A (en) | Aluminum alloy clad tube material excellent in corrosion resistance and heat exchanger incorporating the clad tube material | |
| JP2000202682A (en) | Aluminum alloy brazing material and aluminum alloy clad material for heat exchanger having excellent brazing properties and corrosion resistance using the brazing material as a cladding material | |
| JP2000135588A (en) | High strength aluminum alloy clad material for heat exchanger with excellent corrosion resistance | |
| JP2000135590A (en) | High strength aluminum alloy clad material for heat exchanger | |
| JP2691069B2 (en) | Heat exchanger with excellent corrosion resistance and heat transfer | |
| JP3863595B2 (en) | Aluminum alloy brazing sheet | |
| JP2023045751A (en) | Brazing sheet and manufacturing method of the same | |
| JP2933382B2 (en) | High strength and high corrosion resistance aluminum alloy clad material for heat exchanger | |
| JP2000135591A (en) | Aluminum alloy clad material for heat exchanger with excellent corrosion resistance | |
| JP2006037137A (en) | High corrosion resistance aluminum clad material for heat exchanger |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A621 | Written request for application examination |
Free format text: JAPANESE INTERMEDIATE CODE: A621 Effective date: 20050330 |
|
| A977 | Report on retrieval |
Free format text: JAPANESE INTERMEDIATE CODE: A971007 Effective date: 20060720 |
|
| A131 | Notification of reasons for refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A131 Effective date: 20070223 |
|
| A521 | Request for written amendment filed |
Free format text: JAPANESE INTERMEDIATE CODE: A523 Effective date: 20070424 |
|
| A131 | Notification of reasons for refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A131 Effective date: 20070904 |
|
| A521 | Request for written amendment filed |
Free format text: JAPANESE INTERMEDIATE CODE: A523 Effective date: 20071030 |
|
| A131 | Notification of reasons for refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A131 Effective date: 20080228 |
|
| A521 | Request for written amendment filed |
Free format text: JAPANESE INTERMEDIATE CODE: A523 Effective date: 20080414 |
|
| A131 | Notification of reasons for refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A131 Effective date: 20080724 |
|
| A521 | Request for written amendment filed |
Free format text: JAPANESE INTERMEDIATE CODE: A523 Effective date: 20080818 |
|
| TRDD | Decision of grant or rejection written | ||
| A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 Effective date: 20080911 |
|
| A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 |
|
| A61 | First payment of annual fees (during grant procedure) |
Free format text: JAPANESE INTERMEDIATE CODE: A61 Effective date: 20080916 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20110926 Year of fee payment: 3 |
|
| R150 | Certificate of patent or registration of utility model |
Ref document number: 4190295 Country of ref document: JP Free format text: JAPANESE INTERMEDIATE CODE: R150 Free format text: JAPANESE INTERMEDIATE CODE: R150 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20110926 Year of fee payment: 3 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20120926 Year of fee payment: 4 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20130926 Year of fee payment: 5 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| S111 | Request for change of ownership or part of ownership |
Free format text: JAPANESE INTERMEDIATE CODE: R313115 |
|
| R360 | Written notification for declining of transfer of rights |
Free format text: JAPANESE INTERMEDIATE CODE: R360 |
|
| R350 | Written notification of registration of transfer |
Free format text: JAPANESE INTERMEDIATE CODE: R350 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| EXPY | Cancellation because of completion of term |