JPS59116353A - Composite al alloy sheet for fin material for heat exchanger - Google Patents
Composite al alloy sheet for fin material for heat exchangerInfo
- Publication number
- JPS59116353A JPS59116353A JP23041082A JP23041082A JPS59116353A JP S59116353 A JPS59116353 A JP S59116353A JP 23041082 A JP23041082 A JP 23041082A JP 23041082 A JP23041082 A JP 23041082A JP S59116353 A JPS59116353 A JP S59116353A
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- composition
- unavoidable impurities
- heat exchanger
- core
- 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
Abstract
Description
【発明の詳細な説明】
この発明は、すぐれた高温酊サグ性、物性陽極効果、お
よび熱伝導性を有し、特にろう付りにより熱交すｉ７．
Ｐａ１を製造するに際して、フィン相として用いるの
に適したＡｔ合金複合シートに関するものである。DETAILED DESCRIPTION OF THE INVENTION This invention has excellent high-temperature sag properties, physical anode effects, and thermal conductivity, and is particularly suitable for i7.
The present invention relates to an At alloy composite sheet suitable for use as a fin phase in producing Pa1.
従来、−舶に、例メは自動車のラソエータや、空論機器
斤とにはＡｔ合金製熱交換器が広く使用されている。こ
の熱交抄器は、通常、Ａｔ合金芯月相片面また幻、画面
にＡｔ合金皮相をクラッドしたものからなるＡｔ合合金
金シートで構成されたフィン相を、Ａｔ合金シート、あ
るい１ｄＡｔ合金芯相の片面捷たは両ｊｆ＋１にＡｔ合
金Ｆ！ｉ拐をクラッドしたものからなるＡｔ合合金金シ
ートで構成された管拐に、真空中、不活性ガス中、ある
いはフラックスを用いた大免中で、前記Ａｔ合金の融点
直下の温度である５８０〜６２０℃の温度で、ろう付け
することによって製造されている。Conventionally, heat exchangers made of At alloys have been widely used in ships, for example, automobile lasoators and air-conditioning equipment. This heat exchanger usually uses an At alloy sheet or a 1dAt alloy to replace the fin phase with an At alloy sheet consisting of an At alloy core cladding with an At alloy surface on one side or a screen with an At alloy surface. At alloy F on one side or both jf+1 of the core phase! A tube made of an At alloy sheet made of an At alloy clad with an aluminum alloy is heated to a temperature of 580° C., which is just below the melting point of the At alloy, in a vacuum, an inert gas, or in a heat treatment using a flux. Manufactured by brazing at temperatures of ~620°C.
したがって、上゛記フィン相用複合シートには、ろう付
は時におけるろう劇の溶融温度以上の高温加熱に対して
処刑しない十分な高温耐サグ性、ろうイ」け後に良好な
熱交換性能を発（ｔｌ（する高い熱伝導性、さらに賃料
をよく防食し、さらに貫通孔にまで発展する孔食を発生
させないようにづるための犠性陽極効抹−を具備するこ
とが要求されるが、従来提案されている各種のフィン利
用Ａ２合金複合シートは、いずｉｔもこれらの高温耐サ
グ性、熱伝導性、および犠性陽棒効見のうちの少なくと
もいずれかの特・性に劣るのが現状である。Therefore, the composite sheet for the fin phase described above has sufficient high temperature sag resistance that does not suffer from high temperature heating above the melting temperature of the wax during brazing, and good heat exchange performance after brazing. It is required to have high thermal conductivity (tl), as well as a sacrificial anode to prevent pitting corrosion that can develop into through holes. All of the various A2 alloy composite sheets using fins that have been proposed so far are inferior in at least one of the following properties: high-temperature sag resistance, thermal conductivity, and sacrificial positive bar effectiveness. is the current situation.
そこで、本発明者等は、上述のような観点から、高温配
サグ性、熱伝導性、および物性陽極効果を具イ１１１シ
たＡｔ合金複合シートを得べく研究を行なった結果、Ａ
ｔ合金複合シートにおける世相を、５ｔｅＯ０１〜０．
８％、Ｚｒ ： ０．０２〜０．２０係を合有し、さら
に必要に応じてＭｎ ： ０．１〜０．５％、 Ｃｒ
： （１，０５〜（１，３０％ 、へ４ｇ： ０．１〜
１．５％、およびＣｕ ： （１，０５〜ｆ１．７０％
のうちのｌ ｆ＋＋・または２１巾以」二を含有し、残
りがＡｔと不可北不純物から々る組成を有するＡ−を合
金で構成し、かつｍ１記芯拐の両面にクラッドさｉする
用杓を・、Ｚｎ ： （１，３〜２．０％を含有し、ざ
らに必要に応じてＭｇ：０．１〜１．２％を含有し、残
りがＡｔ と不可避不純物からなる組成（以上ル量チ、
以−トチけすべて重−Ｍ％）を有するＡｔ合金で構成す
ると、この結果のＡｔ合金複合シートは、前記芯旧例よ
ってすぐれたｚ１縣酬サグ性および熱伝導性が確保され
、かつ前記芯材に比して■１気化学的に卑な前記皮相に
よってずぐれた犠件陽橙効果が確保されることから、こ
れを熱交換器のフィン相として用いた切合に幻、ろう付
は時におけるりｊ形がなく、かつろうイ蒐」け後にはず
ぐれた熱伝導性および情性陽棒効果を発揮し、もって熱
交換器の著しく長期にＵる使用を可能にするという知見
を得たのである。Therefore, from the above-mentioned viewpoint, the present inventors conducted research to obtain an At alloy composite sheet that has high-temperature sag distribution properties, thermal conductivity, and physical anode effects, and found that A
The state of affairs in the t-alloy composite sheet was determined from 5teO01 to 0.
8%, Zr: 0.02 to 0.20%, and if necessary, Mn: 0.1 to 0.5%, Cr
: (1,05~(1,30%, 4g: 0.1~
1.5%, and Cu: (1.05~f1.70%
For use in which A- is made of an alloy and has a composition of l f++ or 21 width or more, and the remainder is At and impurities, and cladding is applied to both sides of the m1 core. Zn: (contains 1.3 to 2.0%, if necessary, Mg: 0.1 to 1.2%, and the remainder consists of At and unavoidable impurities (the above) quantity,
The resulting At alloy composite sheet has superior sag resistance and thermal conductivity than the core material, and the core material Compared to ■1, the chemically base phase ensures an excellent sacrificial effect, so it is difficult to cut and braze when using it as the fin phase of a heat exchanger. It has been discovered that the heat exchanger has no shape and exhibits excellent thermal conductivity and a positive effect after it is installed, thereby enabling the use of the heat exchanger for a significantly longer period of time. be.
この発明は、上記知見にもとづいてなされたものであっ
て、１′−ノ、下に成分組成を上記の通シに限定した理
由を説明する。This invention has been made based on the above knowledge, and the reason why the component composition is limited to the above-mentioned structure will be explained below.
Ａ、芯材
（ａ） ＺｒおよびＳｔ
これらの成分は、Ａｔと結合して素地中に微細にして均
一に分散析出するＡｔ Ｚ ｒ Ｓ ｉ 化合物
を形成し、このＡｔ−Ｚｒ−８ｔ 化合物には芯拐の
再結晶温度を上昇させる作用があネので、ろう付は加熱
時に再結晶粒が和犬化するようになり、この和犬再結晶
粒によってろう付は時に変形が発生しないすぐれた茜温
耐サグ性が確保沁れ、さらに前記ｈｔ −Ｚｒ −Ｓｉ
化合物はＡｔ素地のもつすぐれた熱伝導性を阻害し
ない性質をもつので、すぐれた熱伝導性も保持されるよ
うになるが、その含有１ｉ１゛が、それぞれＳｔ：０．
１％未満およびｌｒ ： ０．０２％未満では所望の高
渦削サグ性を確保することができず、一方Ｓｉ： ０−
８％およびＺｒ ａ Ｏ−２０％をそれぞれ越えて含有
させると、前記Ａｔ−Ｚｒ −Ｓｉ化合物の量が多くな
りすぎて熱伝導性に低下傾向が達１．われるようになる
ことから、その含有量を、それぞれＳｉ：０．１〜０，
８％、 Ｚｒ ： ０．０２〜０．２０％と定めた。A. Core material (a) Zr and St These components combine with At to form an At Z r Si compound that is finely dispersed and precipitated uniformly in the substrate, and this At-Zr-8t compound has Since the effect of raising the recrystallization temperature of the core grain is high, the recrystallized grains in brazing become shaped like Japanese dogs when heated, and these Japanese dog recrystallized grains sometimes cause brazing to be made into an excellent madder without deformation. Temperature sag resistance is ensured, and the ht-Zr-Si
Since the compound has the property of not inhibiting the excellent thermal conductivity of the At substrate, it also maintains excellent thermal conductivity.
If Si: less than 1% and lr: less than 0.02%, the desired high vortex cutting sag property cannot be ensured, while Si: 0-
If the content exceeds 8% and Zr a O-20%, the amount of the At-Zr-Si compound becomes too large and the thermal conductivity tends to decrease.1. Si: 0.1 to 0, respectively.
8%, and Zr: 0.02 to 0.20%.
（ｂ） ＭｎおよびＣｒ
これらの成分には、それぞれＡｔと結合してＡｔ−Ｍｎ
−Ｓｉ化合物およびＡｔ −Ｃｒ化合物を形成し、素
地中に微細均一に分散析出して、債：に上記Ａｔ−Ｚｒ
−Ｓｉ化合物との共存において、再結晶粒の粗大化を
一段と促進し、もって芯拐の高温ｌｔ１サグ性をよＣ−
Ｐ向上せしめる作用があるので、特にすぐれた高洛！
ｌＴｉ１ザグ性が要求される場合に心神に応じて含有さ
れるが、その含有ルが、それぞれＭｎ：（１，１％未満
およびＣｒ ： ０−０５ ％未満ではＱｒ望の高福、
附すグ性向上効果がイ（（られず、一方Ｍｎ ： ０−
５チおよびＣｒ ： ０−３０％をおれそれ越兼て含有
させン、と、熱伝Ｎ９伯が低下するようになることから
、その含有弊ヲ、Ｉｕｌｎ ： （１，１〜０．５％Ｉ
ｃｒ：ｏ、ｏｓ〜０．３０％と定と′）た。(b) Mn and Cr These components each have At-Mn bonded to At.
-Si compound and At-Cr compound are formed, finely and uniformly dispersed and precipitated in the substrate, and the At-Zr compound is deposited on the substrate.
- In coexistence with a Si compound, the coarsening of recrystallized grains is further promoted, thereby improving the high temperature lt1 sag property of the core.
It has the effect of increasing P, so it is especially excellent!
When lTi1 zag property is required, it is contained depending on the spirit, but if the content is less than 1.1% of Mn and less than 0-05% of Cr, the quality of Qr is high,
The attached property improvement effect is ((not), while Mn: 0-
If 5 and Cr: 0 to 30% are also contained, the heat transfer N9 ratio will decrease, so the negative effects of their inclusion will be Iuln: (1.1 to 0.5%). I
cr:o,os was constant at ~0.30%.
（ｃ） ＭｇおよびＣｕ
これらの成分には、素地に固溶して、世相の強度を向上
させる作用があるので、特に高弾度が要求される場合に
必要に応じて含有きれるが、その含有量が、それぞれＭ
ｇ：０．１％未満およびＣｕ：０．０５％未満では所望
の強度向上効果が得られず、一方Ｍｇ：１．５％および
Ｃｕ ： ０−７０％をそれぞれ越えて含有させると、
再結晶粒の粗大化が阻害されるようになシ、高温耐ザグ
性が劣化するようになることから、その含有量を、それ
ぞれＭｇ：０．１〜１．５％、 Ｃｕ：０．０５〜０．
７０％と定めた。(c) Mg and Cu These components dissolve in solid solution in the base material and have the effect of improving the strength of the material, so they can be included as necessary when particularly high elasticity is required, but their content is The amount is M
When g: less than 0.1% and Cu: less than 0.05%, the desired strength improvement effect cannot be obtained, while when Mg: 1.5% and Cu: 0-70% are contained, respectively,
Since coarsening of recrystallized grains is inhibited and high-temperature zag resistance is deteriorated, the contents are respectively reduced to Mg: 0.1 to 1.5% and Cu: 0.05. ~0.
It was set at 70%.
Ｂ、皮相
（ａ） Ｚｎ
Ｚｎ成分には、皮材を和気化学的に卑にし、もってフィ
ン相として使用した場合に、十分な犠牲陽極効果を発揮
して管材をよく防食する作用があるが、その含有量が０
．３％未満では所望の犠牲陽極効果を確保することがで
きず、一方２．０％を越えて官有させると、皮相が％Ｉ
′気化学的に岸になり過きてしまい、フィン相としての
帖性陽極効果が促進きれ過きて、フィン材自体の腐食量
が増大するようｌ／Ｃなるばか９でなく、特にｔ空ろう
付けに際して、Ｚｎの参発邦・が多くなって炉汚染の沖
因となることから、その含有１を０．３〜２．０％と定
めた。B. Apparent phase (a) Zn The Zn component has the effect of making the coating chemically base and thereby exerting a sufficient sacrificial anode effect to protect the pipe material from corrosion when used as a fin phase. , its content is 0
．． If it is less than 3%, the desired sacrificial anode effect cannot be ensured, while if it is more than 2.0%, the apparent %I
'It becomes too much vapor chemically, and the pore anode effect as a fin phase is promoted too much, and the amount of corrosion of the fin material itself increases. During brazing, the amount of Zn increases and becomes a cause of furnace contamination, so its content was set at 0.3 to 2.0%.
ｔｂｌ Ｍｇ
ＭｇＤ’ｉ、分には、Ｚｌｌとの共存において皮材をよ
り電気化学的に卑にし、もって犠件陽給効果と面１孔食
Ｇｆｆｉより一段と向上心せる作用があるので、必要に
応じて含有されるが、その含弔陪が帆１％未満では前ｔ
ピ作用に所望の向上効果が得られず、一方１．２％ｆ：
越えて含有させると、加工性が劣化するようになること
から、その含有量を（）、１〜１．２俤と定めた。tbl Mg MgD'i, min has the effect of making the skin material more electrochemically base in coexistence with Zll, thereby improving the sacrificial positive effect and one-plane pitting Gffi, so it can be used as necessary. However, if the content is less than 1%, it is
On the other hand, 1.2% f:
If the content exceeds this amount, the workability deteriorates, so the content was set at 1 to 1.2 yen.
つぎに、この発明のＡｔ合金複合シートを実施例により
具体的に説明する。Next, the At alloy composite sheet of the present invention will be specifically explained using Examples.
実施例
通常の溶ｗｆ鋳造法により、それぞれ組１表に示される
成分組成をもった本発明芯拐用Ａｔ合金１〜２４、従来
芯材用Ａｔ合金２５．２６、本発明皮相用Ａ１合金ａ
、 ｂ、管材用Ａｔ合金、および臂祠のろうｔｌ［Ｊ
Ａｔ合金を溶製し、鋳造して鋳塊とした。なお、これら
の鋳塊は、第１表には表示を省略したが、不可避不純物
として、いずれもＦｅ ： ０−４％以下、Ｚｒ ：
（１，０１％以下、Ｚｎ ： （１，０２φ以下、〜１
１１ ： ｏ、Ｏｔ％以下、Ｍｇ ： ｏ、ｏ １％以
下、ｃｕ ： ０．０１％以下、Ｓｉ ： ０．０７％
以下、およびＣｒ：（１，０１％以下を含有するもので
あった。Examples At alloys 1 to 24 for core materials according to the present invention, At alloys 25.26 for conventional core materials, and A1 alloy a for superficial materials according to the present invention, each having the component composition shown in Table 1, were produced by a conventional hot wf casting method.
, b, At alloy for pipe material, and wax tl[J
An At alloy was melted and cast into an ingot. Although these ingots are not shown in Table 1, they all contain Fe: 0-4% or less and Zr: 0-4% or less as inevitable impurities.
(1,01% or less, Zn: (1,02φ or less, ~1
11: o, Ot% or less, Mg: o, o 1% or less, cu: 0.01% or less, Si: 0.07%
and Cr: (1.01% or less).
ついで、この結果？４ｖられた各種のＡｔ合金鋳塊に熱
間圧延をＭｌｉ して板片：８網の熱延板とし、さらに
本発明皮相用１を合金ａ、ｂ１および賃料のろう利用Ａ
ｔ合金には冷間用りｕ、を廁して板ｈ：１削の冷延ダ・
４とし、引続いて上記枦Ｊ卑：８−の本発明世相月１
Ａｔ合金１〜２４および従来芯材用Ａｔ合金２５．２６
の熱延ｖｔの両面に、上記＆埋：１謔の本発明皮相用Ａ
ｔ合金ａ、ｂの冷延板をそれぞれＰｌね合わせ、熱間圧
妨−にてクラッドして板厚： ２ｍｍとし、官らにこれ
に２℃／ｒｎｉｎ の昇温速度で加熱して温度：３７
０℃に２時間保持の中間焼鈍を幻、さみ々がら冷間圧延
をＮ・シ返し行ない、最終冷間１夕ｊ１率を３０％とす
ることによって本発明Ａｔ合金複合シート１〜４８およ
び従来Ａ７合合金金シート１〜４を・それぞれ製造した
。′＝！た、板ｊリ−：８Ｂの管材用Ａｔ合金の熱延板
の片面には、上記ａ）’Ｊ、 ： １ ａｍの管拐のろ
う材用Ａｔ合金を重ね合わせ、熱間圧延にて板厚：２喘
とし、さらに続いて上記条件の中間焼鈍を行ないながら
冷間圧延をが１１シて板厚：０．４ｍ＋の賃料用Ａｔ合
金初合シートを製造した。Then, what about this result? The ingots of various At alloys were hot-rolled to produce 8-mesh hot-rolled plates, and the superficial use 1 of the present invention was further applied to alloys a, b1, and wax utilization A.
For T-alloy, cold-rolled plate H: 1-cut cold-rolled steel is used.
4, and then the above-mentioned summary: 8- of the present invention social situation month 1
At alloys 1 to 24 and conventional At alloys for core materials 25.26
On both sides of the hot-rolled VT, the above and embedded A of the present invention for superficial use is applied.
Cold-rolled sheets of T-alloys a and b were laminated and clad in a hot press to a thickness of 2 mm, and then heated at a heating rate of 2° C./rnin to a temperature of: 37
The At alloy composite sheets 1 to 48 of the present invention and Conventional A7 alloy sheets 1 to 4 were manufactured, respectively. ′=! In addition, on one side of a hot-rolled sheet of At alloy for pipe materials of J-Lee: 8B, the above-mentioned a) 'J: 1 am of At alloy for pipe material was superimposed, and the sheet was hot-rolled. The sheet was made to have a thickness of 2 mm, and then cold-rolled for 11 times while performing intermediate annealing under the above conditions to produce an At alloy initial sheet for rental use with a thickness of 0.4 m+.
つきに、この結果得られた本発明Ａｔ合金複合シート１
〜４８および従来Ａｔ合金複合シート１〜４について、
高温部１ザグ性試験、電導性試験、および犠性陽極試験
をそれぞれ行なった。Finally, the resulting At alloy composite sheet 1 of the present invention
~48 and conventional At alloy composite sheets 1 to 4,
A high temperature part 1 zag test, an electrical conductivity test, and a sacrificial anode test were conducted.
まず、高渦耐サグ性試験では、幅：３０ｍｍＸ長さ：
１４０ ｍｒの寸法をもった試験片を切出し、この試験
片を、その長さの３０ＴＩｍかステンレス鋼台板から水
平に突き出るように配置し、この状物て、１気圧の望累
ガス雰囲気中、湛朋：６２０℃に５分間加熱保持後の試
験片の１方への垂下値（試験片先端部の肝下高さ）を測
定した。First, in the high vortex sag resistance test, width: 30mm x length:
A test piece with a dimension of 140 mr was cut out, and this test piece was placed so as to protrude horizontally from a stainless steel base plate with a length of 30 TIm, and the test piece was placed in a continuous gas atmosphere of 1 atm. Dwelling: After heating and holding at 620° C. for 5 minutes, the sagging value in one direction of the test piece (height below the liver at the tip of the test piece) was measured.
また、電導性試験では、上記高温附すグ４ｇ′試験後の
試験片のＴ５．導度を測定した。In addition, in the conductivity test, the T5. The conductivity was measured.
寧らに、犠性陽杼試験では、上配冒温面１サグ性試験後
の試験片を用い、このに駒片を１規定の食塩水中に浸漬
し、試験片に局部溶方１が発生したときの箱、位（孔食
電位）全飽和カロメル電極を基準として測定した。また
、さらに、犠性陽極試験で〜
は、上ａ１：本発明Ａｔ合金ネリ自シート１〜４８およ
び従来Ａｔ合金複合シート１〜４のそれぞれから幅：３
０ｍｍＸ表は＝５０即の試験片を、一方上記管材用Ａｔ
合金複合シートからは幅：４０ｒＰｍＸ長さ：５０ｍの
寸法をもった試験片を切出し、前記管Ｈ用Ａｔ合金複合
シートの８賦片をろう材面を」二に水平に僅き、この上
面中央部に長さ方向にそって上ｔｆｒ、本発明Ａｔ合金
複合シート１〜４８および従沫Ａｔ合金複合シート１〜
４の試験片をそれぞれ画伯に立設し、この状神で１頻圧
の窒素ガス雰囲気中、温度二６２０℃に５分間加熱して
、これら両級駒片をろう付けし、ついで１ ｐｐｍのＣ
ｕ４＋イオンを含有する温度：４０℃の水道水中に３０
日間浸僚の水道水浸漬試験、並Ｏ・に３０日間のＣＡＳ
Ｓ試ｈηを行ない、それぞれ管拐用Ａｔ合金複合シート
のｔ面に発生した孔食数および最大孔食深さを測定した
。これらの結果を第２表に示し７た。In addition, in the sacrificial positive shuttle test, the test piece after the upper temperature surface 1 sag test was used, and the piece was immersed in 1N saline solution, and local melting 1 occurred on the test piece. The box position (pitting potential) was measured using a fully saturated calomel electrode as a reference. Further, in the sacrificial anode test, ~ was obtained from each of the upper a1: present invention At alloy Neri self-sheets 1-48 and the conventional At alloy composite sheets 1-4: width: 3
0 mm
A test piece with dimensions of width: 40 rPm x length: 50 m was cut out from the alloy composite sheet, and the 8 pieces of the At alloy composite sheet for pipe H were placed slightly horizontally on the brazing metal surface and in the center of the top surface. In the longitudinal direction, the upper TFR, the At alloy composite sheets 1 to 48 of the present invention, and the conventional At alloy composite sheets 1 to 48,
Each of the test pieces of No. 4 was placed upright in a painter's chair, heated in a nitrogen gas atmosphere at a constant pressure of 1 for 5 minutes at a temperature of 2,620°C, these two grade pieces were brazed, and then 1 ppm of C
Temperature containing u4+ ions: 30% in tap water at 40°C
Tap water immersion test for 1 day, 30 days CAS for average O.
An S test hη was conducted to measure the number of pitting corrosions and the maximum pitting depth that occurred on the t-plane of the At alloy composite sheet for pipe removal. These results are shown in Table 2.
第２表に示される結采から、本発明Ａｔ合合金金シート
】〜４８は、いずれも従来Ａｔ合金作合シー ト１〜４
に片して、一段とすぐれた高湛酬サグ性、熱伝め性、お
よび犠性陽極力°Ｊ果を有し、かつこれらの肴性をずべ
て１（セね備乏ていることが明らかである。From the connections shown in Table 2, the At alloy sheets of the present invention] to 48 are all the conventional At alloy sheets 1 to 4.
On the other hand, it has even better high replenishment sag properties, heat transfer properties, and sacrificial anode strength, and has all of these appetizing properties of 1 (it is clear that the It is.
上述のように、この発明のＡｔ合合金金シートは、すぐ
れた高渦計１サグ性、熱伝梼件、および犠憔陽イへ効果
を具（＃ｆｉ Ｌ、ているので、こｈらの特性が要求き
れる鼻！（９拵器のフィン材とし、て用いた埠合に、Ｉ
Ｃ＝造上および実用上きわめてすぐｉまた件能を発刊【
し、熱交換器の著しく長期にθつでの使用を可能とする
のである。As mentioned above, the At alloy sheet of the present invention has excellent high vortex sag properties, heat conduction conditions, and effects on sacrificial strength. A nose that meets the requirements for the characteristics of 9!
C=Publishing the latest technical and practical information [
This allows the heat exchanger to be used at θ for a significantly longer period of time.
出願人 三菱金属株式会社 代理人 富 １）和 夫 外１名Applicant: Mitsubishi Metals Corporation Agent Tomi 1) Kazuo and 1 other person
Claims (1)
２〜０．２０チを含有し２、残υがＡｔと不可避不純物
からなる組成を有するＡｔ合金で構成され、かつ前記芯
材の両面にクラッドされた支材が、Ｚｎ：０．３〜２．
０チを含イイし、残りがＡｔと不可避不純物からなる組
成（以上小川〕を有するＡ２合金で構成さｉｔたことを
特セ？とする熱交換器フィン材用Ａｔ合金複合シート。 （２） 芯材が、Ｓｉ： ０．１〜０．８ ％、Ｚｒ
：０．０２〜０．２０％を含有し、さらにＭｎ ： （
１，１〜０．５％およびＣｒ ： ０．０５〜０．３０
％のうちの１種または２種を含有し、残りがＡｔ、と不
可避不純物からなる組成を有するＡ７合金で構成され、
かつ前記芯材の両面にクラッドされた皮材が、Ｚｎ ：
０゜３〜２．０％を含有し、残りがＡｔと不可避不純
物からなる組成（以上１量％）を有するＡｔ合金で＃ｉ
ｉｉ成されたことを特徴とする熱交換器フィン拐用Ａｔ
合金初合シート。 （３） 芯材が、Ｓｉ：０．１〜０．８％、Ｚｒ：０
．０２〜０．２０％を含冶し、さらにＭｇ：（１，１〜
１．５チおよびＣｕ ： ０．０５〜０．７０％ の
うちの１種または２種を含有し、残りがＡｔと不可避不
純物からなる組成を有するＡｔ合金で構成され、かつ前
記芯材の両面にクラッドされた皮相が、Ｚｎ ：’ ０
．３〜２．０％を含有し、残りがＡｔと不可避不純物か
らなる組成（以上７Ｊ４釦％）を有するＡｔ合金で構成
されたことを特徴とする熱交換器フィン材用Ａｔ合金接
合シート。 （４） 芯材が、ｓｔ ： ０．１〜ｏ、ｓ％、Ｚｒ
：０．０２〜０．２０％を含有し、さらにＭ、ｎ ：
０．１〜（１，５％およびＣｒ ： ０．０５〜０．３
０ ％のうちの１押または２種と、 Ｍｇ： ０．１〜
１．５ ％およびＣｕ ： ０．０５〜０．７０係のう
ちのｌ柚または２種とを含有し、残りがＡｔと不可避不
純物からなる組成を有するＡｔ合金で構成され、かつ前
記芯材の両面にクラッドさｔ７た皮相が、Ｚｎ ： （
１，３〜２．０％゛／含有し、列・りがＡ）と不ＵｉＪ
避不純物力らなる組成（以上Ｖ量％）を有するＡｔ＠金
で構成されたことを特徴とする熱交挨器フィン相用Ａ７
合金初合シート。 （５） 世相か、Ｓ ｉ： ０−１〜０−８％、 Ｚ
ｒ ： （１，０２〜０１２０％を含有し、残りがＡ
ｔと不可避不純物Ｆからなる組成をイ１゛するＡｔ合金
で構成され、かつ前記芯相の両面にクラッドされた皮相
が、Ｚｎ：ｏ、３〜２．０％を含有し、きらにＭｇ ：
ｏ、ｔ〜１．２％を含有し、熱りかＡｔと不可避不純
物からなる糺ｌル（以上７７１糞１）を楢するパノ合金
で第１ケたソされたことを眉テＰマとする熱シｒ１器フ
インイ’：ｌ’ ＨＩＡｔ合金複合シート。 （６） 芯ｔａ’ ｉ’、Ｓｉ ： ０．１〜０．８
％、 Ｚｒ ： ０．０２〜０．２０％を含有し、づら
にＭｎ ： （１，ｉ 〜０．５ ％およ０’ Ｃｒ
： ０．０５〜０．３０ ％のうちの１ｆＩｌｉｔたけ
２枇を含有し、ダしり〆ｌ’Ａｔと不可避不純物からな
る組成を有するＡｔ合金で構成され、かつ前配芯拐の両
面にクラッドされた皮材が、Ｚｎ ： （＋ −３〜２
．０％を含イ１し、２らにＭｇ ： ｔ、）、ｔ〜１．
２チを含有ｊ〜、残りがＡｔと不ｏＪ避不純物からなる
組成（以上ｍＴｆ：ｔ％）を有するＡｔ合金で構成され
たことを特徴とする熱交（ｆ・イ器フィン相用Ａ／、合
金初合シート。 （７） 芯相が、Ｓｔ： （１，１〜０．８ ％、Ｚ
ｒ ：帆０２〜（１，２０係を含有し、さらにハ嬉：０
．ｊ〜１．５％ネよびＣｕ ： （１，０５〜（１，７
０％のうちのｉ ｆｉトまたｌ： ’２８＋を力有し、
残りがＡｔと不５Ｊ世不純物からなる組成を有するＡｔ
合金で構成され、かつ前記芯相の両面にクラッドされた
＋９４．ｄが、Ｚｎ ： ０ 、３〜２．０％を含有し
、ざらにＭｇ：ｏ、１〜１．２％を含有し、残りがＡｔ
と不ｏＪ避不純物からなる組成（以上ｘＩ−Ｆｉ％）を
有するＡｔ合金で構成されたことを特徴とする熱交Ｊｉ
ｉ、 器フィン利用Ａ１合金複合シート、（８）芯材が
、Ｓｉ ： ０．１〜（１，８％、Ｚｒ ： ０．０２
〜０．２０％を含有し、さらにＭｎ ： ０．１〜０．
５％およびＣｒ：０．０５〜０．３０ ％のうぢの１
ｆＭ ｉ ｋは２移と、Ｍｇ ： ０．１〜１．５％お
よびＣｕ ： ０．０５〜０．７０チのうちの１秒また
は２種とを含有し、残りがＡｌと不可避不純物からなる
組成を有するＡｔ合金で構成ジれ、かつ前記芯Ｉの両面
にクラッドされた皮材が、Ｚｎ ： ０．３〜２．０％
を含有し、畜らにＭｇ：０．１〜１．２％を含有し、残
りがＡｔと不可避不純物から々る組成（以上型開％）を
有するＡｔ合金で構成されたことｆ：ｔｒｆ徴とする熱
交換器フィン利用Ａ１合金複合シート。[Claims] (11 cores I are Si: 0.1 to 0.8%, Zr: 0.0
The supporting material is made of an At alloy having a composition of Zn: 2 to 0.20%, and the remainder υ is At and unavoidable impurities, and is clad on both sides of the core material. ．．
An At alloy composite sheet for heat exchanger fin material, characterized in that it is composed of an A2 alloy having a composition (hereinafter referred to as "Ogawa") containing 0% and the remainder consisting of At and unavoidable impurities. (2) Core material: Si: 0.1-0.8%, Zr
:0.02 to 0.20%, and further contains Mn: (
1,1~0.5% and Cr: 0.05~0.30
%, and the remainder consists of At and unavoidable impurities.
And the skin material clad on both sides of the core material is Zn:
#i is an At alloy having a composition (not less than 1% by weight) containing 0.3 to 2.0% and the remainder consisting of At and unavoidable impurities.
ii. At for heat exchanger fin removal, characterized in that
Alloy initialization sheet. (3) Core material is Si: 0.1 to 0.8%, Zr: 0
．． 02~0.20%, and further contains Mg:(1,1~
1.5% and Cu: 0.05 to 0.70%, and the remainder is At and unavoidable impurities; The apparent surface clad with Zn:' 0
．． 1. An At alloy bonded sheet for a heat exchanger fin material, characterized in that it is made of an At alloy having a composition of 3 to 2.0% and the remainder consisting of At and unavoidable impurities (7J4%). (4) The core material is st: 0.1~o, s%, Zr
: Contains 0.02 to 0.20%, and further contains M, n:
0.1~(1.5% and Cr: 0.05~0.3
One or two types of 0% and Mg: 0.1~
1.5% and Cu: 0.05 to 0.70, and the rest is At alloy having a composition consisting of At and unavoidable impurities, and of the core material. The surface with cladding on both sides is Zn: (
Contains 1.3 to 2.0%/contains A) and non-UiJ
A7 for heat exchanger fin phase, characterized by being composed of At@gold having a composition (above V amount %) consisting of impurity avoidance force
Alloy initialization sheet. (5) Social conditions, S i: 0-1 to 0-8%, Z
r: (Contains 1.02 to 0.120%, the rest is A
The skin layer is composed of an At alloy having a composition of t and unavoidable impurities F, and the superficial phase clad on both sides of the core phase contains 3 to 2.0% of Zn:O, and Mg:
It is assumed that the first layer was made of Pano alloy, which contains 1.2% of O, T and 1.2% of heat, At, and unavoidable impurities. HIAt alloy composite sheet. (6) Core ta'i', Si: 0.1-0.8
%, Zr: 0.02 to 0.20%, Mn: (1,i to 0.5% and 0'Cr
: It is composed of an At alloy containing 0.05 to 0.30% of 1fIlit, and has a composition consisting of backing At and unavoidable impurities, and is clad on both sides of the front core. Zn: (+ -3~2
．． Containing 0%, 1 and 2, Mg: t, ), t~1.
A heat exchanger (F/I for fin phase A/ , alloy initialization sheet. (7) The core phase is St: (1.1 to 0.8%, Z
r: Sail 02~(Contains 1,20 units, and furthermore: 0
．． j~1.5% Neyo and Cu: (1,05~(1,7
i fit or l out of 0%: '28+,
At having a composition in which the remainder consists of At and non-5J impurities
+94. made of alloy and clad on both sides of the core phase. d contains Zn: 0, 3 to 2.0%, roughly contains Mg: o, 1 to 1.2%, and the remainder is At.
A heat exchanger J is characterized in that it is made of an At alloy having a composition (xI-Fi% or more) consisting of
i, A1 alloy composite sheet using vessel fins, (8) core material, Si: 0.1 to (1.8%, Zr: 0.02)
~0.20%, and further contains Mn: 0.1~0.
5% and Cr: 0.05-0.30%
fM i k contains 2 moieties and 1 or 2 of Mg: 0.1 to 1.5% and Cu: 0.05 to 0.70%, and the remainder consists of Al and inevitable impurities. The skin material is made of an At alloy having a composition and is clad on both sides of the core I, and has a Zn content of 0.3 to 2.0%.
f: trf characteristics, containing Mg: 0.1 to 1.2%, and the remainder being composed of an At alloy having a composition consisting of At and unavoidable impurities (the above mold open%). A1 alloy composite sheet using heat exchanger fins.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP23041082A JPS59116353A (en) | 1982-12-24 | 1982-12-24 | Composite al alloy sheet for fin material for heat exchanger |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP23041082A JPS59116353A (en) | 1982-12-24 | 1982-12-24 | Composite al alloy sheet for fin material for heat exchanger |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS59116353A true JPS59116353A (en) | 1984-07-05 |
| JPH0210213B2 JPH0210213B2 (en) | 1990-03-07 |
Family
ID=16907446
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP23041082A Granted JPS59116353A (en) | 1982-12-24 | 1982-12-24 | Composite al alloy sheet for fin material for heat exchanger |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS59116353A (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH01102297A (en) * | 1987-10-14 | 1989-04-19 | Mitsubishi Alum Co Ltd | Aluminum alloy compound fin material for heat exchanger suitable for brazing and corrosion resistance |
| US5125452A (en) * | 1990-09-18 | 1992-06-30 | Sumitomo Light Metal Industries, Ltd. | Aluminum alloy clad material |
| JPH04232222A (en) * | 1990-12-28 | 1992-08-20 | Honda Motor Co Ltd | Aluminum alloy clad material having superior corrosion resistance |
| US5260142A (en) * | 1990-12-28 | 1993-11-09 | Honda Giken Kogyo Kabushiki Kaisha | Corrosion-resistant clad material made of aluminum alloys |
| US5292595A (en) * | 1992-02-18 | 1994-03-08 | Sumitomo Light Metal Industries, Ltd. | Clad aluminum alloy material having high strength and high corrosion resistance for heat exchanger |
| JP2011038163A (en) * | 2009-08-13 | 2011-02-24 | Sumitomo Light Metal Ind Ltd | Aluminum-clad material for heat-exchanger |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5595094A (en) * | 1979-01-16 | 1980-07-18 | Sumitomo Light Metal Ind Ltd | Core of heat-exchanger made of aluminum alloy |
| JPS5641347A (en) * | 1979-09-13 | 1981-04-18 | Furukawa Alum Co Ltd | Aluminum alloy clad for vacuum brazing |
| JPS575840A (en) * | 1980-06-12 | 1982-01-12 | Mitsubishi Alum Co Ltd | Aluminum alloy brazing sheet having excellent pitting- corrosion resistance and high strength |
| JPS5713141A (en) * | 1980-06-27 | 1982-01-23 | Sumitomo Light Metal Ind Ltd | Finely grained material for stringer of airplane with superior corrosion resistance and its manufacture |
| JPS57131339A (en) * | 1981-02-04 | 1982-08-14 | Mitsubishi Alum Co Ltd | Al alloy with superior heat deformation resistance and heat conductivity |
-
1982
- 1982-12-24 JP JP23041082A patent/JPS59116353A/en active Granted
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5595094A (en) * | 1979-01-16 | 1980-07-18 | Sumitomo Light Metal Ind Ltd | Core of heat-exchanger made of aluminum alloy |
| JPS5641347A (en) * | 1979-09-13 | 1981-04-18 | Furukawa Alum Co Ltd | Aluminum alloy clad for vacuum brazing |
| JPS575840A (en) * | 1980-06-12 | 1982-01-12 | Mitsubishi Alum Co Ltd | Aluminum alloy brazing sheet having excellent pitting- corrosion resistance and high strength |
| JPS5713141A (en) * | 1980-06-27 | 1982-01-23 | Sumitomo Light Metal Ind Ltd | Finely grained material for stringer of airplane with superior corrosion resistance and its manufacture |
| JPS57131339A (en) * | 1981-02-04 | 1982-08-14 | Mitsubishi Alum Co Ltd | Al alloy with superior heat deformation resistance and heat conductivity |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH01102297A (en) * | 1987-10-14 | 1989-04-19 | Mitsubishi Alum Co Ltd | Aluminum alloy compound fin material for heat exchanger suitable for brazing and corrosion resistance |
| US5125452A (en) * | 1990-09-18 | 1992-06-30 | Sumitomo Light Metal Industries, Ltd. | Aluminum alloy clad material |
| JPH04232222A (en) * | 1990-12-28 | 1992-08-20 | Honda Motor Co Ltd | Aluminum alloy clad material having superior corrosion resistance |
| US5260142A (en) * | 1990-12-28 | 1993-11-09 | Honda Giken Kogyo Kabushiki Kaisha | Corrosion-resistant clad material made of aluminum alloys |
| US5292595A (en) * | 1992-02-18 | 1994-03-08 | Sumitomo Light Metal Industries, Ltd. | Clad aluminum alloy material having high strength and high corrosion resistance for heat exchanger |
| JP2011038163A (en) * | 2009-08-13 | 2011-02-24 | Sumitomo Light Metal Ind Ltd | Aluminum-clad material for heat-exchanger |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0210213B2 (en) | 1990-03-07 |
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