JP2007092101A - Aluminum alloy clad material excellent in surface joinability on sacrificial anode material surface, and heat-exchanger - Google Patents
Aluminum alloy clad material excellent in surface joinability on sacrificial anode material surface, and heat-exchanger Download PDFInfo
- Publication number
- JP2007092101A JP2007092101A JP2005280665A JP2005280665A JP2007092101A JP 2007092101 A JP2007092101 A JP 2007092101A JP 2005280665 A JP2005280665 A JP 2005280665A JP 2005280665 A JP2005280665 A JP 2005280665A JP 2007092101 A JP2007092101 A JP 2007092101A
- Authority
- JP
- Japan
- Prior art keywords
- sacrificial anode
- anode material
- brazing
- aluminum alloy
- clad
- 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
Images
Landscapes
- Prevention Of Electric Corrosion (AREA)
- Pressure Welding/Diffusion-Bonding (AREA)
Abstract
Description
本発明は、犠牲陽極材面のろう付けによる面接合性に優れたアルミニウム合金クラッド材、とくに、不活性ガス雰囲気中でのフッ化物フラックスを用いたろう付けや真空ろう付けにより接合されるラジエータやヒータなどのアルミニウム合金製熱交換器のチューブ、ヘッダーなど、流体通路構成部材の素材として好適に使用される熱交換器用アルミニウム合金クラッド材および該クラッド材から成形されたチューブを組み付けた熱交換器に関する。 The present invention relates to an aluminum alloy clad material excellent in surface bondability by brazing of a sacrificial anode material surface, in particular, a radiator or a heater bonded by brazing using a fluoride flux in an inert gas atmosphere or vacuum brazing. The present invention relates to an aluminum alloy clad material for a heat exchanger that is suitably used as a material for a fluid passage component such as a tube and header of an aluminum alloy heat exchanger such as the above, and a heat exchanger in which a tube formed from the clad material is assembled.
熱交換器、たとえばラジエータなど、自動車用アルミニウム合金製熱交換器は、作動流体(冷媒)の通路となるチューブ、チューブ間に配設されるフィンおよびヘッダーから構成されている。このような自動車用熱交換器のチューブ材、ヘッダープレート材としては、JIS A3003などのAl−Mn系合金を心材とし、心材の片面にAl−Si系合金ろう材をクラッドした二層構造のアルミニウム合金クラッド材、心材の両面にろう材をクラッドした三層構造のアルミニウム合金クラッド材、あるいは心材の一方の面にろう材をクラッドし他方の面にAl−Zn系合金またはAl−Zn−Mg系合金の犠牲陽極材をクラッドした三層構造のアルミニウム合金クラッド材が用いられている。 A heat exchanger made of aluminum alloy for automobiles such as a radiator, for example, includes a tube serving as a passage for a working fluid (refrigerant), fins disposed between the tubes, and a header. As a tube material and header plate material of such an automobile heat exchanger, an aluminum of a two-layer structure in which an Al—Mn alloy such as JIS A3003 is used as a core and an Al—Si alloy brazing material is clad on one side of the core is used. Alloy clad material, aluminum alloy clad material with a three-layer structure in which brazing material is clad on both sides of the core material, or brazing material is clad on one side of the core material and Al—Zn alloy or Al—Zn—Mg type on the other side A three-layer aluminum alloy clad material clad with an alloy sacrificial anode material is used.
クラッド材のAl−Si系ろう材は、アルミニウム合金製熱交換器を製作するとき、チューブ外面とフィンとの接合、チューブとヘッダープレートとの接合、またはクラッド板からろう付けによりチューブを製造する場合のろう付け接合のためにクラッドされている。これらのろう付には、フッ化物フラックスを用いる不活性ガス雰囲気ろう付け、真空ろう付けが適用される。 When manufacturing an aluminum alloy heat exchanger, the cladding material Al-Si brazing material is used when the tube is joined by joining the outer surface of the tube and the fin, joining the tube and the header plate, or brazing the clad plate. Clad for brazing joints. For these brazings, inert gas atmosphere brazing using a fluoride flux and vacuum brazing are applied.
三層構造のアルミニウム合金クラッド材の犠牲陽極材は、たとえばチューブの内面側に使用され、作動流体と接して犠牲陽極作用を発揮し、心材の孔食や隙間腐食の発生を防止し、チューブ外面に接合されたフィン材は、使用中に犠牲陽極作用を発揮して心材の孔食の発生を防止する。 Sacrificial anode material of aluminum alloy clad material with a three-layer structure is used on the inner surface side of the tube, for example, and exerts sacrificial anode action in contact with the working fluid, preventing the occurrence of pitting corrosion and crevice corrosion of the core material, and the outer surface of the tube The fin material joined to the surface exhibits a sacrificial anodic action during use to prevent the occurrence of pitting corrosion of the core material.
従来、ラジエータやヒータは、図1に示すように、心材5の一方の面にろう材6をクラッドし、他方の面に犠牲陽極材7をクラッドしてなるクラッド板材4を曲成し溶接(溶接部W)して偏平チューブ1とし、ヘッダプレートに組み付けた後一体ろう付けして製造されていた(以下、溶接型)が、近年、図2、図3に示すように、クラッド板材4を曲げ加工するだけで溶接することなくチューブ形状2、3とし、ヘッダプレートに組み付けた後一体ろう付けして製造されることが多くなっている(以下、ろう付け型)。
Conventionally, as shown in FIG. 1, a radiator or a heater is formed by bending and welding a
図2、図3に示すろう付け型においては、不活性ガス雰囲気ろう付けの場合、ろう付け中にチューブ内面の空気が不活性ガスに完全に置換されず残存するため、図2においてはA部、すなわち犠牲陽極材7とろう材6との接合面、図3においてはB部、すなわちチューブ3のT形状の曲げ加工端部と犠牲陽極材7の接合面のろう付け接合が、ろう材が犠牲陽極材面に十分濡れ広がらないために不十分となる場合がある。
In the brazing mold shown in FIGS. 2 and 3, in the case of brazing with an inert gas atmosphere, the air on the inner surface of the tube remains without being completely replaced by the inert gas during brazing. That is, the joining surface of the
熱交換器用アルミニウム合金クラッド材については、これまで、犠牲陽極材の粒界腐食など結晶粒界近傍での腐食を防止する目的に対しては、いくつかの検討が行われており、たとえば犠牲陽極材の厚さ方向の再結晶粒をクラッド材における犠牲陽極材の厚さ未満とすること(特許文献1)、犠牲陽極材のZn含有量を6.0%を越え15.0%以下とする成分構成とし、ろう付後の表面の結晶粒径を100〜700μmとすること(特許文献2)が提案されているが、犠牲陽極材面のろう付け性向上については検討されていない。
発明者らは、上記の問題点を解決するために、犠牲陽極材面のろうの濡れ性におよぼす要因について検討を行った結果、とくに犠牲陽極材の結晶粒度がろうの濡れ性に影響を与え、犠牲陽極材表面のろう付け加熱後の結晶粒度を制御することにより犠牲陽極材のぬれ性が向上し、犠牲陽極材面のろう付けによる面接合性が向上することを見出した。 In order to solve the above problems, the inventors have studied the factors affecting the wettability of the sacrificial anode material surface. As a result, in particular, the crystal grain size of the sacrificial anode material has an effect on the wettability of the wax. The inventors have found that the wettability of the sacrificial anode material is improved by controlling the crystal grain size after brazing heating of the sacrificial anode material surface, and the surface bonding property by brazing of the sacrificial anode material surface is improved.
本発明は、上記の知見に基づいてさらに試験、検討を加えた結果としてなされたものであり、その目的は、熱交換器、とくに自動車搭載用ラジエータやヒータなど、自動車用アルミニウム合金製熱交換器のチューブ材、ヘッダープレート材などとして好適に使用することができ、犠牲陽極材は十分な防食効果を発揮して優れた耐食性を与えるとともに、犠牲陽極材面のろう付けによる面接合性に優れたアルミニウム合金クラッド材を提供することにある。 The present invention has been made as a result of further examination and examination based on the above-mentioned knowledge, and its purpose is a heat exchanger, in particular, an automotive aluminum alloy heat exchanger such as a radiator or a heater mounted on a vehicle. The sacrificial anode material exhibits a sufficient anticorrosion effect to give excellent corrosion resistance, and has excellent surface joining by brazing the sacrificial anode material surface. The object is to provide an aluminum alloy clad material.
上記の目的を達成するための請求項1による犠牲陽極材面のろう付けによる面接合性に優れたアルミニウム合金クラッド材は、犠牲陽極材をクラッドしたアルミニウム合金クラッド材であって、該犠牲陽極材が、Zn:0.5〜5%、Fe:0.1以上0.4%未満、Si:0.01〜1.2%、Mn:0.1〜2.0%を含有してなり、アルミニウム合金クラッド材を、400℃までの昇温速度を50℃/分とし595℃までの到達時間を30分以内とする条件で加熱した場合において、犠牲陽極材の表面の結晶粒度が0.08〜0.20mmであることを特徴とする。
An aluminum alloy clad material excellent in surface bondability by brazing a sacrificial anode material surface according to
請求項2による犠牲陽極材面のろう付けによる面接合性に優れたアルミニウム合金クラッド材は、請求項1において、 前記犠牲陽極材がさらにCr:0.02〜0.3%、Zr:0.02〜0.3%、Ti:0.01〜0.35%のうちの1種または2種以上を含有することを特徴とする。
The aluminum alloy clad material excellent in surface bondability by brazing the sacrificial anode material surface according to
請求項3による犠牲陽極材面のろう付けによる面接合性に優れたアルミニウム合金クラッド材は、請求項1または2において、前記犠牲陽極材がさらにIn:0.001〜0.05%、Sn:0.001〜0.05%の1種または2種を含有することを特徴とする。
The aluminum alloy clad material excellent in surface bondability by brazing the sacrificial anode material surface according to
請求項4による犠牲陽極材面のろう付けによる面接合性に優れたアルミニウム合金クラッド材は、請求項1〜3のいずれかにおいて、心材の一方の面にろう材をクラッドし、他方の面に犠牲陽極材をクラッドした三層構造であることを特徴とする。
The aluminum alloy clad material excellent in surface bondability by brazing of the sacrificial anode material surface according to
請求項5による犠牲陽極材面のろう付けによる面接合性に優れたアルミニウム合金クラッド材は、請求項1〜4のいずれかにおいて、ろう付けにより犠牲陽極材面を面接合することによって製造される熱交換器用チューブ材として用いられることを特徴とする。
The aluminum alloy clad material excellent in surface bonding property by brazing the sacrificial anode material surface according to
請求項6による熱交換器は、請求項1〜4のいずれかに記載のアルミニウム合金クラッド材を熱交換器用チューブに成形し、成形されたチューブと、フィンおよびヘッダーを組み付けて、一体にろう付け接合してなることを特徴とする。
A heat exchanger according to
本発明によれば、熱交換器、とくに不活性ガス雰囲気中でのフッ化物フラックスを用いるろう付けや真空ろう付けにより接合される自動車搭載用ラジエータやヒータなど、自動車用アルミニウム合金製熱交換器のチューブ材、ヘッダープレート材などとして好適に使用することができ、犠牲陽極材は十分な防食効果を発揮して優れた耐食性を与えるとともに、犠牲陽極材面のろう付けによる面接合性に優れたアルミニウム合金クラッド材が提供される。 According to the present invention, a heat exchanger, particularly a heat exchanger made of aluminum alloy for automobiles such as a radiator or heater for automobiles joined by brazing using a fluoride flux in an inert gas atmosphere or vacuum brazing. Aluminum that can be used favorably as a tube material, header plate material, etc., and the sacrificial anode material provides excellent corrosion resistance by providing a sufficient anticorrosion effect, and also has excellent surface bonding by brazing the sacrificial anode material surface An alloy cladding material is provided.
本発明のアルミニウム合金クラッド材は犠牲陽極材の組成およびろう付け加熱後の結晶粒度を特徴とするものであり、その組成およびその限定理由について説明する。
(犠牲陽極材)
Zn:0.5〜5.0%
Znは、犠牲陽極材の電位を卑にし、心材に対する犠牲陽極効果を発揮させ、心材の孔食または隙間腐食の発生を防止する。Znの好ましい含有量は0.5〜5.0%の範囲であり、Znの含有量が0.5%未満ではその効果が小さく、5.0%を越えて含有すると犠牲陽極材の自己耐食性が低下する。Znのより好ましい含有範囲は1.5〜5.0%であり、Znの含有量の下限を1.5%とすることによりさらに優れた犠牲陽極効果を発揮させることができる。
The aluminum alloy clad material of the present invention is characterized by the composition of the sacrificial anode material and the crystal grain size after brazing heating, and the composition and the reason for the limitation will be described.
(Sacrificial anode material)
Zn: 0.5 to 5.0%
Zn lowers the potential of the sacrificial anode material, exerts a sacrificial anode effect on the core material, and prevents the core material from pitting or crevice corrosion. The preferable content of Zn is in the range of 0.5 to 5.0%. If the Zn content is less than 0.5%, the effect is small, and if it exceeds 5.0%, the self-corrosion resistance of the sacrificial anode material Decreases. A more preferable content range of Zn is 1.5 to 5.0%. By setting the lower limit of the Zn content to 1.5%, a more excellent sacrificial anode effect can be exhibited.
Fe:0.1〜0.4%未満
Feは、犠牲陽極材のろう付け加熱後の結晶粒を微細化し、ろう付け加熱後の結晶粒度を低下させる。Fe含有量が0.4%を越えるとろう付け加熱後の結晶粒度が微細になりすぎるとともに、ろう付け時に部分的に溶融が生じ、また犠牲陽極材の自己耐蝕性が低下する。Feの好ましい含有量は0.4%未満であり、0.1%未満では効果が十分でない。Feのさらに好ましい含有範囲は0.1〜0.3%である。
Fe: Less than 0.1 to 0.4% Fe refines the crystal grains after brazing heating of the sacrificial anode material, and reduces the crystal grain size after brazing heating. If the Fe content exceeds 0.4%, the crystal grain size after brazing heating becomes too fine, melting occurs partly during brazing, and the self-corrosion resistance of the sacrificial anode material decreases. The preferable content of Fe is less than 0.4%, and if it is less than 0.1%, the effect is not sufficient. The more preferable content range of Fe is 0.1 to 0.3%.
Si:0.01〜1.2%
Siは、犠牲陽極材の強度を向上させるとともに、犠牲陽極材のろう付け加熱後の結晶粒を微細化し、結晶粒度を低下させる。Si含有量が1.2%を越えると犠牲陽極材の融点が低下して、ろう付け時に部分溶融が生じ犠牲陽極効果が低下する。0.01%未満では地金コストが高くなり実用上好ましくない。Siのさらに好ましい含有範囲は0.1〜0.5%である。
Si: 0.01-1.2%
Si improves the strength of the sacrificial anode material, refines the crystal grains after brazing heating of the sacrificial anode material, and reduces the crystal grain size. If the Si content exceeds 1.2%, the melting point of the sacrificial anode material is lowered, and partial melting occurs during brazing, thereby reducing the sacrificial anode effect. If it is less than 0.01%, the bullion cost becomes high, which is not practically preferable. The more preferable content range of Si is 0.1 to 0.5%.
Mn:0.1〜2.0%
Mnは、犠牲陽極材の強度を向上させるとともに、犠牲陽極材のろう付け加熱後の結晶粒を微細化し、結晶粒度を低下させる。Mn含有量が2.0%を越えると犠牲陽極材の自己耐食性が低下する。0.1%未満では効果が十分でない。Mnのさらに好ましい含有範囲は0.6〜1.4%である。
Mn: 0.1 to 2.0%
Mn improves the strength of the sacrificial anode material, refines the crystal grains after brazing heating of the sacrificial anode material, and reduces the crystal grain size. If the Mn content exceeds 2.0%, the self-corrosion resistance of the sacrificial anode material decreases. If it is less than 0.1%, the effect is not sufficient. A more preferable content range of Mn is 0.6 to 1.4%.
Cr:0.02〜0.3%、Zr:0.02〜0.3%、Ti:0.01〜0.35%
Cr、ZrおよびTiは、材料の板厚方向に濃度の高い領域と濃度の低い領域に分かれ、これらの領域が層状となって交互に分布し、各元素の濃度の低い領域が高い領域に比べて優先的に腐食するため、腐食形態が層状となり、従って板厚方向への粒界腐食の進行が妨げられて材料の耐孔食性が向上する。
Cr: 0.02-0.3%, Zr: 0.02-0.3%, Ti: 0.01-0.35%
Cr, Zr, and Ti are divided into a high concentration region and a low concentration region in the thickness direction of the material, and these regions are alternately distributed in layers, and the low concentration region of each element is higher than the high region. Therefore, the corrosion form becomes layered, and therefore the progress of intergranular corrosion in the thickness direction is hindered to improve the pitting corrosion resistance of the material.
CrおよびZrの好ましい含有量は0.02〜0.3%の範囲であり、0.02%未満ではその効果が十分でなく、0.3%を超えて含有しても効果が飽和してそれ以上の改善が得られない。CrおよびZrのさらに好ましい含有範囲は0.05〜0.2%である。Tiの好ましい含有量は0.01〜0.35%の範囲であり、0.01%未満ではその効果が小さく、0.35%を超えて含有すると、鋳造時に粗大な晶出物が生成し、また加工性が低下して健全な材料の製造が困難となる。Tiのさらに好ましい含有範囲は0.06〜0.3%である。 The preferable content of Cr and Zr is in the range of 0.02 to 0.3%. If the content is less than 0.02%, the effect is not sufficient, and even if the content exceeds 0.3%, the effect is saturated. No further improvement can be obtained. A more preferable content range of Cr and Zr is 0.05 to 0.2%. The preferable content of Ti is in the range of 0.01 to 0.35%. When the content is less than 0.01%, the effect is small. When the content exceeds 0.35%, a coarse crystallized product is produced during casting. In addition, the processability is lowered, making it difficult to produce a sound material. A more preferable content range of Ti is 0.06 to 0.3%.
In:0.001〜0.05%、Sn:0.001〜0.05%
InとSnは、微量の添加によって犠牲陽極材の電位を卑とし、犠牲陽極効果によって心材の孔食や隙間腐食の発生を防止する。InとSnの好ましい含有量は0.001〜0.05%の範囲であり、0.001%未満ではその効果が十分でなく、0.05%を越えると自己耐食性および圧延加工性が低下する。InとSnのさらに好ましい含有範囲は0.01〜0.02%である。本発明においては、V:0.01〜0.3%、B:0.01〜0.3%、Cu:0.2%以下の1種以上を添加しても同様の効果が得られる。
In: 0.001-0.05%, Sn: 0.001-0.05%
In and Sn lower the potential of the sacrificial anode material by adding a small amount, and prevent the occurrence of pitting corrosion and crevice corrosion of the core material by the sacrificial anode effect. The preferable contents of In and Sn are in the range of 0.001 to 0.05%. If the content is less than 0.001%, the effect is not sufficient. . A more preferable content range of In and Sn is 0.01 to 0.02%. In the present invention, the same effect can be obtained by adding one or more of V: 0.01 to 0.3%, B: 0.01 to 0.3%, and Cu: 0.2% or less.
本発明によるアルミニウム合金クラッド材は、心材の一方の面にろう材、他方の面に犠牲陽極材をクラッドした3層構造のクラッド材、心材の片面に犠牲陽極材をクラッドした2層構造のクラッド材、心材の両面に犠牲陽極材をクラッドした3層構造のクラッド材に適用される。心材の一方の面にろう材、他方の面に犠牲陽極材をクラッドした3層構造のクラッド材に適用する場合、心材、ろう材としては、たとえば以下に示すように、通常実用化されているアルミニウム合金を使用することができる。 The aluminum alloy clad material according to the present invention has a three-layer clad material in which a brazing material is clad on one surface of a core material, a sacrificial anode material is clad on the other surface, and a two-layer clad material in which a sacrificial anode material is clad on one surface of the core material. It is applied to a clad material having a three-layer structure in which a sacrificial anode material is clad on both surfaces of a material and a core material. When applied to a clad material having a three-layer structure in which a brazing material is clad on one surface of the core material and a sacrificial anode material is clad on the other surface, the core material and the brazing material are usually put into practical use as shown below, for example. Aluminum alloys can be used.
(心材)
心材としては、A3003に代表されるAl−Mn系合金、より高強度なAl−Si−Mn系合金、Al−Cu−Mn系合金、Al−Si−Cu−Mn系合金などを使用することができる。また、それぞれの合金にMgを添加した合金も使用することができる。各合金に、さらにTi、Zn、Cr、Zr、V、Bなどを含んでいても同様の効果が得られる。
(Heartwood)
As the core material, an Al-Mn alloy represented by A3003, a higher strength Al-Si-Mn alloy, an Al-Cu-Mn alloy, an Al-Si-Cu-Mn alloy, or the like may be used. it can. Also, alloys obtained by adding Mg to the respective alloys can be used. The same effect can be obtained even if Ti, Zn, Cr, Zr, V, B, etc. are further contained in each alloy.
(ろう材)
ろう材としては、通常用いられているAl−Si系合金、例えばSi:6〜13%を含むAl−Si合金が使用される。ラジエータなどを構成するために行われるろう付けが真空ろう付けの場合には、Al−Si−Mg系合金などが用いられる。これらのAl−Si系合金、Al−Si−Mg系合金には、必要に応じて、Bi:0.2%以下、Be:0.1%以下、Ca:1.0%以下、Li:1.0%以下、Sr:0.005〜0.1%が添加されてもよい。
(Brazing material)
As the brazing material, a commonly used Al—Si alloy, for example, an Al—Si alloy containing Si: 6 to 13% is used. When the brazing performed to form a radiator or the like is vacuum brazing, an Al—Si—Mg alloy or the like is used. These Al—Si based alloys and Al—Si—Mg based alloys include Bi: 0.2% or less, Be: 0.1% or less, Ca: 1.0% or less, Li: 1, as necessary. 0.0% or less and Sr: 0.005 to 0.1% may be added.
(400℃までの昇温速度を50℃/分とし595℃までの到達時間を30分以内とする条件で加熱した場合の犠牲陽極材の表面の結晶粒度:0.08〜0.20mm)
本発明においては、犠牲陽極材の表面の結晶粒度を、上記の加熱条件で加熱した場合に0.08〜0.20mmとすることが重要である。上記の加熱条件はろう付け加熱の条件に相当し、犠牲陽極材の表面の結晶粒度が上記の加熱条件で0.08〜0.20mmとなれば、通常のろう付け加熱後における犠牲陽極材の表面の結晶粒度を略0.08〜0.20mmとすることができる。
(The crystal grain size of the surface of the sacrificial anode material when heated at a rate of temperature increase to 400 ° C. of 50 ° C./min and an arrival time of 595 ° C. within 30 minutes: 0.08 to 0.20 mm)
In the present invention, it is important that the crystal grain size on the surface of the sacrificial anode material is 0.08 to 0.20 mm when heated on the above heating conditions. The above heating conditions correspond to the conditions for brazing heating. If the crystal grain size of the surface of the sacrificial anode material is 0.08 to 0.20 mm under the above heating conditions, the sacrificial anode material after normal brazing heating is used. The crystal grain size of the surface can be set to about 0.08 to 0.20 mm.
犠牲陽極材表面へろうが濡れ拡がる場合、結晶粒界が優先的にろうの濡れ拡がる経路になり、その後、ろうは結晶粒界から粒内方向へ濡れ拡がる。従って、結晶粒度が小さい場合、濡れ拡がる経路が多くなり、ろうは均一に濡れ拡がる。一方、結晶粒度が大きい場合、濡れ拡がる経路が少なく、ろうの濡れ拡がりは不均一になり、濡れ性が低下する。ろうの濡れ性が良好である犠牲陽極材の結晶粒度は、犠牲陽極材の表面からみて0.08〜0.20mmの範囲であり、0.20mmを超えると濡れ拡がり性は低下し、結晶粒度が0.08mm以下ではこの効果が飽和する。結晶粒度のさらに好ましい範囲は0.08〜0.15mmである When the wax spreads to the surface of the sacrificial anode material, the grain boundary is preferentially a path through which the wax spreads, and then the wax wets and spreads inward from the crystal grain boundary. Therefore, when the crystal grain size is small, there are many routes for wetting and spreading, and the wax spreads uniformly. On the other hand, when the crystal grain size is large, there are few routes for wetting and spreading, the wetting and spreading of wax becomes non-uniform, and the wettability decreases. The crystal grain size of the sacrificial anode material with good brazing wettability is in the range of 0.08 to 0.20 mm when viewed from the surface of the sacrificial anode material, and when it exceeds 0.20 mm, the wetting and spreading properties are reduced. If this is 0.08 mm or less, this effect is saturated. A more preferable range of the crystal grain size is 0.08 to 0.15 mm.
本発明のアルミニウム合金クラッド材の製造は、例えばアルミニウム合金クラッド材の構成材となる心材、犠牲陽極材およびろう材を構成するアルミニウム合金を、連続鋳造により造塊し、得られた鋳塊を、心材については均質化処理し、ろう材については必要に応じて均質化処理した後、所定厚さまで熱間圧延し、犠牲陽極材については固相線温度(℃)×0.7以上の温度で均質化処理した後、所定厚さまで熱間圧延し、ついで、心材用アルミニウム合金鋳塊と、熱間圧延された犠牲陽極用アルミニウム合金およびろう材用アルミニウム合金を組み合わせて、常法に従って熱間圧延によりクラッド材とし、その後冷間圧延、350℃以下の中間焼鈍、加工度20〜35%の冷間圧延により所定の厚さとすることにより行われる。 Production of the aluminum alloy clad material of the present invention, for example, the core material constituting the aluminum alloy clad material, the sacrificial anode material and the aluminum alloy constituting the brazing material, ingot by continuous casting, the ingot obtained, The core material is homogenized, the brazing material is homogenized as necessary, and then hot-rolled to a predetermined thickness. The sacrificial anode material is at a solidus temperature (° C.) × 0.7 or higher. After homogenization treatment, hot-roll to a predetermined thickness, then hot-roll in accordance with conventional methods by combining the aluminum alloy ingot for core material with the hot-rolled aluminum alloy for sacrificial anode and aluminum alloy for brazing material Then, a clad material is used, and then cold rolling, intermediate annealing at 350 ° C. or lower, and cold rolling at a workability of 20 to 35% are performed to obtain a predetermined thickness.
本発明において、400℃までの昇温速度を50℃/分とし595℃までの到達時間を30分以内とする条件で加熱した場合の犠牲陽極材の表面の結晶粒度を0.08〜0.20mmの範囲に制御するためには、犠牲陽極材の鋳塊を、犠牲陽極材の固相線温度(℃)×0.7以上の温度で均質化処理するとともに、中間焼鈍温度を350℃以下にし、中間焼鈍後の冷間圧延の加工度を20〜35%にするのが有効である。 In the present invention, the crystal grain size on the surface of the sacrificial anode material when heated at a rate of temperature increase to 400 ° C. of 50 ° C./min and an arrival time of 595 ° C. within 30 minutes is 0.08 to 0.005. In order to control to a range of 20 mm, the ingot of the sacrificial anode material is homogenized at a temperature equal to or higher than the solidus temperature of the sacrificial anode material (° C.) × 0.7 and the intermediate annealing temperature is 350 ° C. or less. It is effective to make the degree of cold rolling after intermediate annealing 20 to 35%.
本発明のアルミニウム合金クラッド材を成形して、図2〜3に示すチューブ形状とし、該チューブとともに、アルミニウム合金フィンおよびアルミニウム合金からなるヘッダーを組み付け、一体にろう付け接合することにより、ラジエータ、ヒータなどの自動車用熱交換器が製造される。 The aluminum alloy clad material of the present invention is molded into a tube shape shown in FIGS. 2 to 3, and a header made of an aluminum alloy fin and an aluminum alloy is assembled together with the tube, and brazed together to form a radiator and a heater. Such as automotive heat exchangers.
以下、本発明の実施例を比較例と対比して説明する。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。 Examples of the present invention will be described below in comparison with comparative examples. These examples show one embodiment of the present invention, and the present invention is not limited to these examples.
実施例1
連続鋳造によって表1に示す組成を有する心材用合金、表2に示す組成を有する犠牲陽極材用合金および表3に示す組成を有するろう材用合金を造塊し、得られた鋳塊のうち、心材用合金および犠牲陽極材用合金の鋳塊については常法に従って均質化処理を行った。犠牲陽極材の均質化処理温度は550℃(犠牲陽極材の固相線温度(℃)×0.7以上の温度)とした。
Example 1
Among the ingots obtained by ingot-making the alloy for core material having the composition shown in Table 1, the alloy for sacrificial anode material having the composition shown in Table 2, and the alloy for brazing material having the composition shown in Table 3 by continuous casting. The ingots of the core material alloy and the sacrificial anode material alloy were homogenized according to a conventional method. The homogenization temperature of the sacrificial anode material was set at 550 ° C. (solidus temperature (° C.) of sacrificial anode material × 0.7 or higher temperature).
ついで、犠牲陽極材用合金およびろう材用合金の鋳塊を所定の厚さまで熱間圧延し、これらの熱間圧延板と心材用合金の鋳塊(厚さ30mm)とを合わせ材として熱間圧延し、三層構造のクラッド材(厚さ3mm)を得た。その後、冷間圧延、中間焼鈍(温度350℃)、加工度30%の冷間圧延を行って、厚さ0.20mmの板材(クラッド材)を得た。クラッド材の構成は、犠牲陽極材は0.040mm、ろう材は0.035mmである。 Next, the ingot of the alloy for sacrificial anode material and the alloy for brazing material is hot-rolled to a predetermined thickness, and the hot-rolled sheet and the ingot of alloy for core material (thickness 30 mm) are combined as a hot material. Rolling was performed to obtain a clad material having a three-layer structure (thickness: 3 mm). Thereafter, cold rolling, intermediate annealing (temperature 350 ° C.), and cold rolling with a workability of 30% were performed to obtain a plate material (cladding material) having a thickness of 0.20 mm. The structure of the clad material is 0.040 mm for the sacrificial anode material and 0.035 mm for the brazing material.
得られたクラッド材を試験材として、以下の方法により犠牲陽極材の表面(L−LT面)の結晶粒度を測定し、犠牲陽極材面のろう付けによる面接合性、ろうの濡れ広がり性を評価した。結果を表4に示す。
(結晶粒度の測定)
クラッド材(試験材)にフッ化物フラックスを塗布し、窒素ガス中、595℃(材料温度)に加熱した。但し、400℃までは50℃/分の昇温速度で加熱した。595℃の温度への到達時間は20分であった。加熱後の試験材を、リン酸400mL、硫酸100mLと無水クロム酸25gを混合した溶液中で、電圧30Vで1〜3分電解研磨し、さらに、純水500mL、フッ酸27mL(46%)、ホウ酸11gを混合した溶液中で、電圧25〜30Vで45〜60秒電解研磨した。その後、光学顕微鏡を用いて犠牲陽極材表面の偏光ミクロ組織を撮影し、比較法により結晶粒度を測定した。比較にはASTM(E112−61)の標準結晶粒度組織図を用いた。
Using the obtained clad material as a test material, the crystal grain size of the surface (L-LT surface) of the sacrificial anode material is measured by the following method, and surface bondability and brazing wettability of the sacrificial anode material surface are measured. evaluated. The results are shown in Table 4.
(Measurement of crystal grain size)
Fluoride flux was applied to the clad material (test material) and heated to 595 ° C. (material temperature) in nitrogen gas. However, it heated at the temperature increase rate of 50 degree-C / min up to 400 degreeC. The time to reach a temperature of 595 ° C. was 20 minutes. The test material after heating was electropolished in a mixed solution of phosphoric acid 400 mL, sulfuric acid 100 mL and chromic anhydride 25 g for 1 to 3 minutes at a voltage of 30 V. Furthermore, pure water 500 mL, hydrofluoric acid 27 mL (46%), Electropolishing was performed at a voltage of 25 to 30 V for 45 to 60 seconds in a solution mixed with 11 g of boric acid. Thereafter, the polarization microstructure on the surface of the sacrificial anode material was photographed using an optical microscope, and the crystal grain size was measured by a comparative method. The standard grain size structure chart of ASTM (E112-61) was used for comparison.
(犠牲陽極材面のろう付けによる面接合性の評価)
得られたクラッド板材を用いて、垂直板の端部を直角に折り曲げ、垂直板にだけフッ化物フラックスを5g/m2塗布した後、図4の通り組み合わせて隙間充填試験片を作成し、窒素ガス中で595℃(材料温度)に加熱した。但し、400℃までは50℃/分の昇温速度で加熱した。図4において、数値は長さ(単位mm)を示す。
加熱後の隙間充填試験片の隙間充填長さFL(図5)をノギスを用いて測定した。ろう付け性による面接合性の評価は、隙間充填長さが8.0mm以上を良好(○)とし、8.0mm未満を不良(×)とした。
(Evaluation of surface bondability by brazing the sacrificial anode material surface)
Using the obtained clad plate material, the end of the vertical plate was bent at a right angle, and after applying 5 g / m 2 of fluoride flux only to the vertical plate, a gap filling test piece was prepared by combining as shown in FIG. Heated to 595 ° C. (material temperature) in gas. However, it heated at the temperature increase rate of 50 degree-C / min up to 400 degreeC. In FIG. 4, the numerical value indicates the length (unit: mm).
Void filling length of the gap filling test piece after heating F L (Figure 5) was measured using calipers. In the evaluation of the surface bonding property by brazing, a gap filling length of 8.0 mm or more was evaluated as good (◯), and less than 8.0 mm was evaluated as defective (×).
(犠牲陽極材面のろうの濡れ広がり性の評価)
得られたクラッド板材を用いて、20mm×60mmの板を切り出し、シェーパ加工により端面(4面全て)を切削し15mm×55mmに仕上げた。この板をフラックスを塗布することなく、犠牲陽極材を上にして炉内に水平に設置し、窒素ガス中でろう付け温度(材料温度)595℃で加熱した。但し、400℃までは50℃/分の昇温速度で加熱した。加熱後の犠牲陽極材面を光学顕微鏡を用いて16倍で撮影した写真(ネガポジ反転撮影)(図6)上からろう周り平均長さL(例えば、図6においてはL=(L1+L2)/2)を測定した。ろうの濡れ広がり性の評価は、ろう周り平均長さLが1.5mm以上を良好(○)、1.5mm未満を不良(×)とした。
(Evaluation of wax spreading on sacrificial anode material surface)
Using the obtained clad plate material, a 20 mm × 60 mm plate was cut out, and the end surfaces (all four surfaces) were cut by a shaper process to finish 15 mm × 55 mm. Without applying the flux, this plate was placed horizontally in the furnace with the sacrificial anode material facing up, and heated at a brazing temperature (material temperature) of 595 ° C. in nitrogen gas. However, it heated at the temperature increase rate of 50 degree-C / min up to 400 degreeC. A photograph of the sacrificial anode material surface after heating taken at a magnification of 16 using an optical microscope (negative-positive reversal photography) (FIG. 6) From above the average length L around the wax (for example, L = (L1 + L2) / 2 in FIG. 6) ) Was measured. In the evaluation of the wetting and spreading property of the wax, the average length L around the wax was 1.5 mm or more as good (◯), and less than 1.5 mm as bad (x).
表4にみられるように、本発明に従う試験材No.1〜25はいずれも、犠牲陽極材面のろう付けによる面接合性、ろうの濡れ広がり性が優れていた。 As seen in Table 4, the test material No. All of Nos. 1 to 25 were excellent in surface bondability by brazing of the surface of the sacrificial anode material, and wettability of the brazing.
比較例1
連続鋳造によって表5に示す組成を有する犠牲陽極材用合金を造塊し、得られた鋳塊については550℃の温度で均質化処理を行った。ついで、犠牲陽極材用合金の鋳塊および実施例1で造塊したろう材用合金の鋳塊を所定の厚さまで熱間圧延し、これらの熱間圧延板と実施例1で造塊した心材用合金の鋳塊(厚さ30mm)とを合わせ材として熱間圧延し、三層構造のクラッド材(厚さ3mm)とした。その後、冷間圧延、中間焼鈍(温度500℃)、加工度70%の冷間圧延によって厚さ0.20mmの板材(クラッド材)を得た。クラッド材の構成は、犠牲陽極材は0.080mm、ろう材は0.035mmである。
Comparative Example 1
An alloy for a sacrificial anode material having the composition shown in Table 5 was ingoted by continuous casting, and the resulting ingot was homogenized at a temperature of 550 ° C. Next, the ingot of the alloy for sacrificial anode material and the ingot of the alloy for brazing material ingoted in Example 1 were hot-rolled to a predetermined thickness, and these hot-rolled plates and the core material ingoted in Example 1 were hot rolled. An alloy ingot (thickness 30 mm) was hot-rolled as a laminated material to obtain a three-layer clad material (
得られたクラッド材を試験材として、実施例1と同じ方法で犠牲陽極材表面の結晶粒度(L−LT面)を測定し、犠牲陽極材面のろう付けによる面接合性、ろうの濡れ広がり性を評価した。結果を表6に示す。 Using the obtained clad material as a test material, the crystal grain size (L-LT surface) of the surface of the sacrificial anode material was measured in the same manner as in Example 1, and the surface bondability by brazing the sacrificial anode material surface and the wetting spread of the brazing Sex was evaluated. The results are shown in Table 6.
表6に示すように、試験材26はFeの含有量が少ないため犠牲陽極材の結晶粒度が大きく、ろう付けによる面接合性、ろうの濡れ広がり性が劣る。試験材27は中間焼鈍温度、中間焼鈍後の冷間圧延加工度が高いことに起因して犠牲陽極材の結晶粒度が小さくなり、ろう付けによる面接合性の評価およびろうの濡れ広がり性評価の加熱において犠牲陽極材に局部溶融が生じた。 As shown in Table 6, since the test material 26 has a small Fe content, the crystal grain size of the sacrificial anode material is large, and the surface bonding property by brazing and the wetting and spreading property of the brazing are inferior. In the test material 27, the grain size of the sacrificial anode material is reduced due to the intermediate annealing temperature and the high degree of cold rolling after the intermediate annealing, and the evaluation of the surface bondability by brazing and the evaluation of the wetting spreadability of the brazing Local melting occurred in the sacrificial anode material upon heating.
1 クラッド板材を曲成、溶接して形成した扁平チューブ
2 クラッド板材を曲げ加工するだけで形成したチューブの実施例
3 クラッド板材を曲げ加工するだけで形成したチューブの他の実施例
4 クラッド板材
5 心材
6 ろう材
7 犠牲陽極材
DESCRIPTION OF
Claims (6)
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2005280665A JP4623729B2 (en) | 2005-09-27 | 2005-09-27 | Aluminum alloy clad material and heat exchanger excellent in surface bonding by brazing of sacrificial anode material surface |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2005280665A JP4623729B2 (en) | 2005-09-27 | 2005-09-27 | Aluminum alloy clad material and heat exchanger excellent in surface bonding by brazing of sacrificial anode material surface |
Publications (2)
Publication Number | Publication Date |
---|---|
JP2007092101A true JP2007092101A (en) | 2007-04-12 |
JP4623729B2 JP4623729B2 (en) | 2011-02-02 |
Family
ID=37978151
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP2005280665A Active JP4623729B2 (en) | 2005-09-27 | 2005-09-27 | Aluminum alloy clad material and heat exchanger excellent in surface bonding by brazing of sacrificial anode material surface |
Country Status (1)
Country | Link |
---|---|
JP (1) | JP4623729B2 (en) |
Cited By (14)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2007277706A (en) * | 2006-03-13 | 2007-10-25 | Sumitomo Light Metal Ind Ltd | Aluminum alloy clad material for heat exchanger having excellent strength and brazability |
JP2008127607A (en) * | 2006-11-17 | 2008-06-05 | Furukawa Sky Kk | Aluminum alloy clad plate |
WO2008078598A1 (en) * | 2006-12-27 | 2008-07-03 | Kabushiki Kaisha Kobe Seiko Sho | Aluminum alloy brazing sheet for heat exchanger |
JP2008261026A (en) * | 2007-04-13 | 2008-10-30 | Denso Corp | High-strength and high-melting point aluminum alloy clad plate for heat exchanger having excellent durability, method for producing the same, and heat exchanger made of aluminum alloy |
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 |
JP2009161827A (en) * | 2008-01-09 | 2009-07-23 | Sumitomo Light Metal Ind Ltd | Brazing sheet for tube material of heat exchanger, and method for producing heat exchanger using the same |
JP2010255015A (en) * | 2009-04-21 | 2010-11-11 | Sumitomo Light Metal Ind Ltd | Clad material for welded tube of heat exchanger made from aluminum alloy, and method for manufacturing the same |
JP2010255014A (en) * | 2009-04-21 | 2010-11-11 | Sumitomo Light Metal Ind Ltd | Clad material for welded tube of heat exchanger made from aluminum alloy, and method for manufacturing the same |
JP2010540882A (en) * | 2007-09-26 | 2010-12-24 | ヴァレオ システム テルミク | Heat exchanger material coating |
JP2012207276A (en) * | 2011-03-30 | 2012-10-25 | Kobe Steel Ltd | Aluminum alloy brazing sheet |
JP2013234376A (en) * | 2012-05-11 | 2013-11-21 | Furukawa-Sky Aluminum Corp | High strength aluminum alloy brazing sheet and method for manufacturing the same |
CN115308088A (en) * | 2022-08-15 | 2022-11-08 | 吉林大学 | Multifunctional clamp for solderability test, testing method and application |
WO2023203296A1 (en) * | 2022-04-19 | 2023-10-26 | Constellium Neuf-Brisach | Heat exchanger based on an alumnimium alloy obtained by brazing |
Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH03124393A (en) * | 1989-10-05 | 1991-05-27 | Furukawa Alum Co Ltd | Brazing sheet for refrigerant passage for heat exchanger made of al |
JP2004035966A (en) * | 2002-07-05 | 2004-02-05 | Sumitomo Light Metal Ind Ltd | Aluminum alloy clad material and its manufacturing process |
JP2004076057A (en) * | 2002-08-13 | 2004-03-11 | Sumitomo Light Metal Ind Ltd | Aluminum alloy clad plate and method for producing the same |
JP2005232506A (en) * | 2004-02-18 | 2005-09-02 | Sumitomo Light Metal Ind Ltd | Aluminum alloy clad material for heat exchanger |
JP2005232507A (en) * | 2004-02-18 | 2005-09-02 | Sumitomo Light Metal Ind Ltd | Aluminum alloy clad material for heat exchanger |
-
2005
- 2005-09-27 JP JP2005280665A patent/JP4623729B2/en active Active
Patent Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH03124393A (en) * | 1989-10-05 | 1991-05-27 | Furukawa Alum Co Ltd | Brazing sheet for refrigerant passage for heat exchanger made of al |
JP2004035966A (en) * | 2002-07-05 | 2004-02-05 | Sumitomo Light Metal Ind Ltd | Aluminum alloy clad material and its manufacturing process |
JP2004076057A (en) * | 2002-08-13 | 2004-03-11 | Sumitomo Light Metal Ind Ltd | Aluminum alloy clad plate and method for producing the same |
JP2005232506A (en) * | 2004-02-18 | 2005-09-02 | Sumitomo Light Metal Ind Ltd | Aluminum alloy clad material for heat exchanger |
JP2005232507A (en) * | 2004-02-18 | 2005-09-02 | Sumitomo Light Metal Ind Ltd | Aluminum alloy clad material for heat exchanger |
Cited By (15)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2007277706A (en) * | 2006-03-13 | 2007-10-25 | Sumitomo Light Metal Ind Ltd | Aluminum alloy clad material for heat exchanger having excellent strength and brazability |
JP2008127607A (en) * | 2006-11-17 | 2008-06-05 | Furukawa Sky Kk | Aluminum alloy clad plate |
WO2008078598A1 (en) * | 2006-12-27 | 2008-07-03 | Kabushiki Kaisha Kobe Seiko Sho | Aluminum alloy brazing sheet for heat exchanger |
US8227091B2 (en) | 2006-12-27 | 2012-07-24 | Kobe Steel, Ltd. | Aluminum alloy brazing sheet for heat exchanger |
JP2008261026A (en) * | 2007-04-13 | 2008-10-30 | Denso Corp | High-strength and high-melting point aluminum alloy clad plate for heat exchanger having excellent durability, method for producing the same, and heat exchanger made of aluminum alloy |
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 |
JP2010540882A (en) * | 2007-09-26 | 2010-12-24 | ヴァレオ システム テルミク | Heat exchanger material coating |
JP2009161827A (en) * | 2008-01-09 | 2009-07-23 | Sumitomo Light Metal Ind Ltd | Brazing sheet for tube material of heat exchanger, and method for producing heat exchanger using the same |
JP2010255014A (en) * | 2009-04-21 | 2010-11-11 | Sumitomo Light Metal Ind Ltd | Clad material for welded tube of heat exchanger made from aluminum alloy, and method for manufacturing the same |
JP2010255015A (en) * | 2009-04-21 | 2010-11-11 | Sumitomo Light Metal Ind Ltd | Clad material for welded tube of heat exchanger made from aluminum alloy, and method for manufacturing the same |
JP2012207276A (en) * | 2011-03-30 | 2012-10-25 | Kobe Steel Ltd | Aluminum alloy brazing sheet |
JP2013234376A (en) * | 2012-05-11 | 2013-11-21 | Furukawa-Sky Aluminum Corp | High strength aluminum alloy brazing sheet and method for manufacturing the same |
WO2023203296A1 (en) * | 2022-04-19 | 2023-10-26 | Constellium Neuf-Brisach | Heat exchanger based on an alumnimium alloy obtained by brazing |
CN115308088A (en) * | 2022-08-15 | 2022-11-08 | 吉林大学 | Multifunctional clamp for solderability test, testing method and application |
Also Published As
Publication number | Publication date |
---|---|
JP4623729B2 (en) | 2011-02-02 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP4623729B2 (en) | Aluminum alloy clad material and heat exchanger excellent in surface bonding by brazing of sacrificial anode material surface | |
JP4702797B2 (en) | Manufacturing method of aluminum alloy clad material excellent in surface bondability by brazing of sacrificial anode material surface | |
JP5714387B2 (en) | Aluminum alloy brazing sheet and heat exchanger | |
JP6452626B2 (en) | Aluminum alloy clad material and method for producing the same, heat exchanger using the aluminum alloy clad material, and method for producing the same | |
JP6006421B2 (en) | Aluminum alloy clad material, method for producing the same, and heat exchanger using the aluminum alloy clad material | |
JP4993440B2 (en) | High strength aluminum alloy clad material for heat exchangers with excellent brazeability | |
JP4807826B2 (en) | Aluminum alloy clad material with excellent surface bonding by brazing sacrificial anode material | |
JP6452627B2 (en) | Aluminum alloy clad material and method for producing the same, heat exchanger using the aluminum alloy clad material, and method for producing the same | |
JP5893450B2 (en) | Aluminum alloy brazing sheet for header of heat exchanger, method for producing the same, and method for producing heat exchanger | |
JP4832354B2 (en) | Aluminum alloy clad material for high strength, high melting point heat exchanger excellent in durability, its manufacturing method, and aluminum alloy heat exchanger | |
JP6418714B2 (en) | Aluminum alloy clad material and method for producing the same, heat exchanger using the aluminum alloy clad material, and method for producing the same | |
JP2008261025A (en) | Aluminum alloy-clad material for heat exchanger having high strength, high melting point and superior durability, manufacturing method thereof, and heat exchanger made from aluminum alloy | |
JP2002161323A (en) | Aluminum alloy fin-material for heat exchanger superior in formability and brazability | |
JP4916333B2 (en) | Aluminum alloy clad material for heat exchangers with excellent strength and brazing | |
JP5836695B2 (en) | Aluminum alloy fin material for heat exchangers with excellent strength and corrosion resistance after brazing | |
JP5279277B2 (en) | Brazing sheet for tube material of heat exchanger, heat exchanger and manufacturing method thereof | |
JP2007277707A (en) | Aluminum alloy clad material for heat exchanger having excellent strength and brazability | |
JP2010197002A (en) | Tube for plate bending-type aluminum heat exchanger, aluminum heat exchanger, and method of manufacturing tube for plate bending-type aluminum heat exchanger | |
JP4993439B2 (en) | High strength aluminum alloy clad material for heat exchangers with excellent brazeability | |
JP2005232506A (en) | Aluminum alloy clad material for heat exchanger | |
JP2005232507A (en) | Aluminum alloy clad material for heat exchanger | |
JP2008013844A (en) | Clad aluminum alloy material for heat exchanger and process for producing the same | |
JP4954551B2 (en) | Aluminum brazing alloy in which erosion during brazing is suppressed, brazing sheet using the same, header pipe for heat exchanger, and heat exchanger | |
JP2001170793A (en) | High-strength aluminum alloy clad metal for heat exchanger excellent in tube manufacturing property and corrosion resistance | |
JPH1088265A (en) | Aluminum alloy fin material for heat exchanger, excellent in sacrificial anode effect as well as in strength after brazing |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
A621 | Written request for application examination |
Free format text: JAPANESE INTERMEDIATE CODE: A621 Effective date: 20071212 |
|
A977 | Report on retrieval |
Free format text: JAPANESE INTERMEDIATE CODE: A971007 Effective date: 20100721 |
|
A131 | Notification of reasons for refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A131 Effective date: 20100727 |
|
A521 | Written amendment |
Free format text: JAPANESE INTERMEDIATE CODE: A523 Effective date: 20100917 |
|
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: 20101028 |
|
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: 20101101 |
|
R150 | Certificate of patent or registration of utility model |
Ref document number: 4623729 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: 20131112 Year of fee payment: 3 |
|
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 |
|
S111 | Request for change of ownership or part of ownership |
Free format text: JAPANESE INTERMEDIATE CODE: R313117 |
|
R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
R350 | Written notification of registration of transfer |
Free format text: JAPANESE INTERMEDIATE CODE: R350 |