JP4669712B2 - Brazing fin material and manufacturing method thereof - Google Patents
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本発明はブレージング用フィン材およびその製造方法に関する。 The present invention relates to a brazing fin material and a method for producing the same.
ブレージングによってラジエータなどの自動車用熱交換器に使用されるフィン材は、従来、コルゲート成形され、チューブ材と組み合わせてろう付接合される。近年熱交換器の軽量化、コスト低減の要求がますます高まり、フィン材はじめ主要部材の薄肉化がさらに進行している。フィン材を薄くする際、熱交換器の特性を維持、向上するため、近年のフィン材はさまざまな元素を添加したり、工程を検討することによって、高強度化を実現している。例えば添加元素を変更した例として、強度と熱伝導性に優れたＡｌ−Ｆｅ−Ｎｉ系合金フィン材（特許文献１，２参照）が提案されている。しかし、この合金はフィンの薄肉化のためには、自己耐食性に関し課題の残る合金であった。また、工程を検討した例として、連続鋳造圧延での冷却速度を規定して強度および導電性を高めたＡｌ−Ｆｅ−Ｍｎ−Ｓｉ系合金フィン材（特許文献３参照）があるが、特許文献３中に記載されているとおり、このフィン材は素材の再結晶粒径が極端に小さい。従ってろう付中にろう拡散によってフィン材が座屈する可能性が高く、薄肉化には適さない。特許文献４ではろう付後強度、熱伝導性、自己耐食性、および耐エロージョン性に優れたフィン材が提案されている。しかしながら、概文献に記載のフィン材の最終冷間圧延率は１５〜５０％であるが、最終冷間圧延率が１５％と５０％では、素材強度、結晶組織形状が大きく異なるのは明白であり、これは耐エロージョン性について考慮されていないことを示している。また、概文献の実施例を見ると、全ての実施例における中間焼鈍は１分未満の連続式焼鈍を用いている。最終板厚と最終冷間圧延率から逆算すると、板厚０．１１ｍｍにおいて連続式焼鈍を行っており、これは工業用設備においてはかなり困難な、限定された設備でのみ実施可能な条件といえる。一般的な連続式焼鈍炉は、コスト、性能の点から板厚０．３〜１．０ｍｍで実施することが前提とされている。例えば板厚０．３ｍｍにおいて連続焼鈍を行い、その後０．０８ｍｍまで冷間圧延するとすると、最終冷間圧延率は７０％を超え、エロージョンが発生する可能性が極めて高い。 A fin material used for a heat exchanger for an automobile such as a radiator by brazing is conventionally corrugated and brazed in combination with a tube material. In recent years, the demand for weight reduction and cost reduction of heat exchangers has been increasing, and the thinning of main members such as fin materials has further progressed. In order to maintain and improve the characteristics of the heat exchanger when thinning the fin material, recent fin materials have been improved in strength by adding various elements and studying the process. For example, as an example in which the additive element is changed, an Al—Fe—Ni alloy fin material excellent in strength and thermal conductivity (see Patent Documents 1 and 2) has been proposed. However, this alloy has remained a problem with respect to self-corrosion resistance for fin thinning. Further, as an example of examining the process, there is an Al—Fe—Mn—Si alloy fin material (see Patent Document 3) whose strength and conductivity are increased by specifying a cooling rate in continuous casting and rolling. 3, the fin material has an extremely small recrystallized grain size. Therefore, there is a high possibility that the fin material buckles by brazing diffusion during brazing, and it is not suitable for thinning. Patent Document 4 proposes a fin material having excellent strength after brazing, thermal conductivity, self-corrosion resistance, and erosion resistance. However, although the final cold rolling rate of the fin material described in the general literature is 15 to 50%, it is obvious that the material strength and the crystal structure shape are greatly different between the final cold rolling rates of 15% and 50%. Yes, this indicates that erosion resistance is not considered. Moreover, when the Example of general literature is seen, the intermediate annealing in all the Examples uses the continuous annealing for less than 1 minute. Back-calculating from the final plate thickness and the final cold rolling rate, continuous annealing is performed at a plate thickness of 0.11 mm, which is a condition that can be implemented only with limited facilities, which is quite difficult in industrial facilities. . A general continuous annealing furnace is assumed to be implemented with a plate thickness of 0.3 to 1.0 mm from the viewpoint of cost and performance. For example, when continuous annealing is performed at a plate thickness of 0.3 mm and then cold rolling is performed to 0.08 mm, the final cold rolling rate exceeds 70%, and erosion is extremely likely to occur.
さらに、特許文献５では双ロール連続鋳造圧延を用いることにより、高強度・高熱伝導性を有するフィン材を提案している。このフィン材はろう付加熱まで圧延組織（繊維状組織）を保持することによって耐ろう拡散性を高めている。しかしながら、ろう付加熱まで圧延組織を有する材料の内部には大量のひずみが残存して、素材の強度が高くなる恐れがある。フィン素材強度が高いと、スプリングバック量が多いことから、フィン材の成形性が低下し、コルゲートやプレス成形を行えない可能性がある。また、素材強度が高いとコバ等から割れが生じ、薄肉での圧延中にコイルが破断する問題もある。 Furthermore, Patent Document 5 proposes a fin material having high strength and high thermal conductivity by using twin roll continuous casting rolling. This fin material enhances the diffusion resistance of the brazing by holding the rolling structure (fibrous structure) up to the brazing heat. However, a large amount of strain remains in the material having a rolled structure up to the brazing heat, and the strength of the material may be increased. If the strength of the fin material is high, the amount of springback is large, so the moldability of the fin material is reduced, and corrugation or press molding may not be possible. Further, when the strength of the material is high, cracks occur from the edge and the like, and there is a problem that the coil breaks during rolling with a thin wall.
以上のように、フィン材の薄肉化には、ろう付加熱後の強度、導電率、耐食性、ろう付中の耐ろう拡散性に優れるだけでなく、安定に生産するために圧延性をはじめとした生産性を材料面から考慮する必要がある。
本発明は、ろう付加熱後の強度、熱伝導性、自己耐食性、ろう付加熱中の耐ろう拡散性、並びにコルゲート成形性に優れたブレージング用フィン材、およびそのフィン材を安定に製造可能な製造方法を提供することを目的とする。 The present invention relates to a brazing fin material excellent in strength after brazing addition heat, heat conductivity, self-corrosion resistance, brazing diffusion resistance during brazing addition heat, and corrugated moldability, and production capable of stably producing the fin material. It aims to provide a method.
本発明は、
（１）０．８ｍａｓｓ％以上２．０ｍａｓｓ％以下のＳｉ、１．０ｍａｓｓ％を超え３．０ｍａｓｓ％以下のＭｎ、０．１０ｍａｓｓ％を超え０．７ｍａｓｓ％未満のＦｅ、残部がＡｌおよび不可避不純物からなり、中間焼鈍前に焼鈍を行うことなく、板厚０．１ｍｍ以下にて最後に行う中間焼鈍後に、表層から見た表面積の８０％以上が圧延方向に長さ１０ｍｍ以上の径を有する再結晶粒によって占められる結晶組織を持つアルミニウム合金を板厚圧下率３０％未満で冷間圧延して製造されたことを特徴とするブレージング用フィン材、
（２）０．８ｍａｓｓ％以上２．０ｍａｓｓ％以下のＳｉ、１．０ｍａｓｓ％を超え３．０ｍａｓｓ％以下のＭｎ、０．１０ｍａｓｓ％を超え０．７ｍａｓｓ％未満のＦｅ、（ａ）３．０ｍａｓｓ％以下のＺｎ、０．３ｍａｓｓ％以下のＩｎ、０．３％ｍａｓｓ以下のＳｎの１種または２種以上、および／または（ｂ）０．２５ｍａｓｓ％以下のＣｕ、０．１ｍａｓｓ％以下のＴｉ、０．１ｍａｓｓ％以下のＺｒの１種または２種以上、および／または（ｃ）０．２ｍａｓｓ％以下のＮｉ、０．２ｍａｓｓ％以下のＣｒ、０．２ｍａｓｓ％以下のＣｏの１種または２種以上、残部がＡｌおよび不可避不純物からなる組成の合金であって、中間焼鈍前に焼鈍を行うことなく、板厚０．１ｍｍ以下にて最後に行う中間焼鈍後に、表層から見た表面積の８０％以上が圧延方向に長さ１０ｍｍ以上の径を有する再結晶粒によって占められる結晶組織を持つアルミニウム合金を板厚圧下率３０％未満で冷間圧延して製造されたことを特徴とするブレージング用フィン材、
（３）前記最後の中間焼鈍を３００〜４８０℃、３０〜１５０分で行うことを特徴とする（１）又は（２）記載のブレージング用フィン材、
（４）０．８ｍａｓｓ％以上２．０ｍａｓｓ％以下のＳｉ、１．０ｍａｓｓ％を超え３．０ｍａｓｓ％以下のＭｎ、０．１０ｍａｓｓ％を超え０．７ｍａｓｓ％未満のＦｅ、残部がＡｌおよび不可避不純物からなるアルミニウム合金を、中間焼鈍前に焼鈍を行うことなく、板厚０．１ｍｍ以下にて最終の中間焼鈍を行い、表層から見た表面積の８０％以上が圧延方向に長さ１０ｍｍ以上の径を有する再結晶粒によって占められる結晶組織を有するようにし、その後板厚圧下率３０％未満で冷間圧延することを特徴とするブレージング用フィン材の製造方法、
（５）０．８ｍａｓｓ％以上２．０ｍａｓｓ％以下のＳｉ、１．０ｍａｓｓ％を超え３．０ｍａｓｓ％以下のＭｎ、０．１０ｍａｓｓ％を超え０．７ｍａｓｓ％未満のＦｅ、（ａ）３．０ｍａｓｓ％以下のＺｎ、０．３ｍａｓｓ％以下のＩｎ、０．３％ｍａｓｓ以下のＳｎの１種または２種以上、および／または（ｂ）０．２５ｍａｓｓ％以下のＣｕ、０．１ｍａｓｓ％以下のＴｉ、０．１ｍａｓｓ％以下のＺｒの１種または２種以上、および／または（ｃ）０．２ｍａｓｓ％以下のＮｉ、０．２ｍａｓｓ％以下のＣｒ、および０．２ｍａｓｓ％以下のＣｏの１種また２種以上、残部がＡｌおよび不可避不純物からなる組成の合金を、中間焼鈍前に焼鈍を行うことなく、板厚０．１ｍｍ以下にて最終の中間焼鈍を行い、表層から見た表面積の８０％以上が圧延方向に長さ１０ｍｍ以上の径を有する再結晶粒によって占められる結晶組織を有するようにし、その後板厚圧下率３０％未満で冷間圧延することを特徴とするブレージング用フィン材の製造方法、および
（６）前記最終の中間焼鈍を３００〜４８０℃、３０〜１５０分で行うことを特徴とする（４）又は（５）記載のブレージング用フィン材の製造方法
を提供するものである。
The present invention
(1) Si of 0.8 mass% or more and 2.0 mass% or less, Mn of more than 1.0 mass% and 3.0 mass% or less, Fe of more than 0.10 mass% and less than 0.7 mass% , the balance being Al and inevitable impurities 80% or more of the surface area seen from the surface layer has a diameter of 10 mm or more in the rolling direction after the intermediate annealing finally performed at a sheet thickness of 0.1 mm or less without annealing before the intermediate annealing. A brazing fin material characterized by being produced by cold rolling an aluminum alloy having a crystal structure occupied by crystal grains at a sheet thickness reduction of less than 30%,
(2) Si of 0.8 mass% or more and 2.0 mass% or less, Mn of more than 1.0 mass% and 3.0 mass% or less, Fe of more than 0.10 mass% and less than 0.7 mass%, (a) 3.0 mass % Or less of Zn, 0.3 mass% or less of In, 0.3% or less of Sn or less of one or more of Sn, and / or (b) 0.25 mass% or less of Cu, 0.1 mass% or less of Ti 1 type or 2 types or more of Zr of 0.1 mass% or less, and / or (c) 1 type or 2 of Ni of 0.2 mass% or less, Cr of 0.2 mass% or less, Co of 0.2 mass% or less seed above, it alloys der compositions the balance of Al and inevitable impurities, without performing annealing before intermediate annealing, after the intermediate annealing carried out at the end at the plate thickness 0.1mm or less, the table as viewed from the surface layer And characterized in that more than 80% of the product has been produced by cold rolling an aluminum alloy having a crystal structure that is occupied by recrystallized grains with a diameter of more than a length of 10mm in the rolling direction in the sheet thickness reduction rate less than 30% Fin material for brazing,
(3) The last intermediate annealing is performed at 300 to 480 ° C. for 30 to 150 minutes, the brazing fin material according to (1) or (2),
(4) Si of 0.8 mass% or more and 2.0 mass% or less, Mn exceeding 1.0 mass% and 3.0 mass% or less, Fe exceeding 0.10 mass% and less than 0.7 mass% , the balance being Al and inevitable impurities The final intermediate annealing is performed at a sheet thickness of 0.1 mm or less without annealing the aluminum alloy before intermediate annealing, and the surface area viewed from the surface layer has a diameter of 10 mm or more in the rolling direction. A method for producing a brazing fin material, characterized by having a crystal structure occupied by the recrystallized grains, and then cold rolling at a sheet thickness reduction of less than 30%,
(5) Si of 0.8 mass% or more and 2.0 mass% or less, Mn of more than 1.0 mass% and 3.0 mass% or less, Fe of over 0.10 mass% and less than 0.7 mass%, (a) 3.0 mass % Or less of Zn, 0.3 mass% or less of In, 0.3% or less of Sn or less of one or more of Sn, and / or (b) 0.25 mass% or less of Cu, 0.1 mass% or less of Ti 1 type or 2 types or more of Zr of 0.1 mass% or less, and / or (c) 1 type of Ni of 0.2 mass% or less, Cr of 0.2 mass% or less, and Co of 0.2 mass% or less 2 or more, the alloy of the composition and the balance of Al and inevitable impurities, without performing annealing before intermediate annealing, carried out the final intermediate annealing at a thickness 0.1mm or less, the surface area as viewed from the surface layer A brazing fin material characterized in that 80% or more has a crystal structure occupied by recrystallized grains having a diameter of 10 mm or more in the rolling direction, and then cold-rolled at a sheet thickness reduction of less than 30% Manufacturing method, and
(6) The method for producing a brazing fin material according to (4) or (5), wherein the final intermediate annealing is performed at 300 to 480C for 30 to 150 minutes. is there.
本発明では薄肉化が進むフィン材の特性を改善できる。具体的には、薄肉化の際に必要である垂下量（熱交換器組み付け製造時の強度）、耐フィン溶け性（耐ろう拡散）、コルゲート成形性および自己耐食性を現在まで使用されているフィン材と同等の性能を維持しつつ、ろう付加熱後の引張強さと熱伝導性を向上できる。さらに本発明は、これらの高性能フィン材を安定に製造することができる。 In the present invention, the characteristics of the fin material that is becoming thinner can be improved. Specifically, fins that have been used up to now for the amount of droop (strength when assembled with heat exchanger), fin melting resistance (wax diffusion resistance), corrugated formability and self-corrosion resistance required for thinning The tensile strength and thermal conductivity after brazing heat can be improved while maintaining the same performance as the material. Furthermore, this invention can manufacture these high performance fin materials stably.
本発明の一つの実施態様は、０．８ｍａｓｓ％以上２．０ｍａｓｓ％以下のＳｉ、１．０ｍａｓｓ％を超え３．０ｍａｓｓ％以下のＭｎ、０．１０ｍａｓｓ％を超え０．７ｍａｓｓ％未満のＦｅ、残部がＡｌおよび不可避不純物からなり、中間焼鈍前に焼鈍を行うことなく、板厚０．１ｍｍ以下にて最後に行う中間焼鈍後に、表層から見た表面積の８０％以上が圧延方向に長さ１０ｍｍ以上の径を有する再結晶粒によって占められる結晶組織を持つアルミニウム合金を板厚圧下率３０％未満で冷間圧延して製造されたブレージング用フィン材である。
One embodiment of the present invention includes: 0.8 mass% to 2.0 mass% Si; 1.0 mass% to 3.0 mass% Mn; 0.10 mass% to less than 0.7 mass% Fe 2 ; The balance is made of Al and inevitable impurities, and 80% or more of the surface area seen from the surface layer is 10 mm in length in the rolling direction after the final annealing at the plate thickness of 0.1 mm or less without annealing before the intermediate annealing. A brazing fin material produced by cold rolling an aluminum alloy having a crystal structure occupied by recrystallized grains having the above diameters at a sheet thickness reduction of less than 30%.
また、本発明の別の実施態様は、０．８ｍａｓｓ％以上２．０ｍａｓｓ％以下のＳｉ、１．０ｍａｓｓ％を超え３．０ｍａｓｓ％以下のＭｎ、０．１０ｍａｓｓ％を超え０．７ｍａｓｓ％未満のＦｅ、残部がＡｌおよび不可避不純物からなるアルミニウム合金を、中間焼鈍前に焼鈍を行うことなく、板厚０．１ｍｍ以下にて最終の中間焼鈍を行い、表層から見た表面積の８０％以上が圧延方向に長さ１０ｍｍ以上の径を有する再結晶粒によって占められる結晶組織を有するようにし、その後板厚圧下率３０％未満で冷間圧延するブレージング用フィン材の製造方法である。
In another embodiment of the present invention, Si is 0.8 mass% or more and 2.0 mass% or less, Mn is more than 1.0 mass% and 3.0 mass% or less, is more than 0.10 mass% and is less than 0.7 mass%. The final intermediate annealing is performed at a thickness of 0.1 mm or less without annealing an aluminum alloy composed of Fe and the balance Al and inevitable impurities before intermediate annealing, and 80% or more of the surface area seen from the surface layer is rolled. This is a method for producing a brazing fin material that has a crystal structure occupied by recrystallized grains having a diameter of 10 mm or more in the direction and then cold-rolled at a sheet thickness reduction of less than 30%.
本発明において、フィン材に用いられるアルミニウム（Ａｌ）合金の組成を上記のように限定した理由を以下に説明する。
本発明ではＡｌ−Ｆｅ−Ｍｎ−Ｓｉ系金属間化合物が微細に分散し、それらが中間焼鈍時に転位や亜結晶粒界の移動を妨げる効果によって、粗大な再結晶組織を得ることが目的である。必須元素のうちケイ素（Ｓｉ）、マンガン（Ｍｎ）はフィン材のろう付後の強度向上、Ｓｉ、Ｍｎ、鉄（Ｆｅ）は微細な金属間化合物を得て、再結晶の粗大化を図る目的で含有させる。
The reason why the composition of the aluminum (Al) alloy used for the fin material in the present invention is limited as described above will be described below.
In the present invention, an Al-Fe-Mn-Si intermetallic compound is finely dispersed, and it is an object to obtain a coarse recrystallized structure due to the effect of preventing dislocations and movement of subgrain boundaries during intermediate annealing. . Among the essential elements, silicon (Si) and manganese (Mn) improve the strength after brazing of the fin material, and Si, Mn and iron (Fe) obtain fine intermetallic compounds to increase the recrystallization. To contain.
Ｍｎの含有量が１．０ｍａｓｓ％以下では十分な強度が得られない。また、再結晶を粗大化させるための微細な第二相分散粒子の数も不足する。逆にＭｎの添加量が３．０ｍａｓｓ％を超えるとろう付前の素材強度が高くなり圧延性が低下する。また、第二相分散粒子のほとんどがＦｅ、Ｓｉを含まないＡｌ６Ｍｎとなる。Ａｌ６Ｍｎの化合物はサイズが小さいため、ろう付によってほとんどが固溶してしまい、フィン材の導電率が低下してしまう。上記理由より１．１ｍａｓｓ％を超え、２．４ｍａｓｓ％以下の範囲が好ましい。 If the Mn content is 1.0 mass% or less, sufficient strength cannot be obtained. In addition, the number of fine second phase dispersed particles for coarsening the recrystallization is insufficient. On the other hand, if the amount of Mn added exceeds 3.0 mass%, the strength of the material before brazing is increased and the rollability is lowered. Further, most of the second phase dispersed particles are Al 6 Mn containing no Fe or Si. Since Al 6 Mn compounds are small in size, most of them are solid-dissolved by brazing and the conductivity of the fin material is lowered. For the above reasons, a range of more than 1.1 mass% and less than 2.4 mass% is preferable.
Ｓｉの含有量が少ない場合も金属間化合物の大部分がＡｌ−Ｍｎ系の化合物となる。この点で０．８ｍａｓｓ％未満では含有量が不十分である。また、２．０ｍａｓｓ％を超えると合金の融点が低下し、ブレージング用フィン材として用いる場合に高確率でろう拡散が生じてしまう。上記理由からより好ましい範囲は０．８５ｍａｓｓ％以上１．６ｍａｓｓ％以下である。 Even when the Si content is small, most of the intermetallic compounds are Al-Mn compounds. In this respect, if it is less than 0.8 mass%, the content is insufficient. Moreover, when it exceeds 2.0 mass%, melting | fusing point of an alloy will fall, and when it uses as a fin material for brazing, wax diffusion will arise with high probability. For the above reason, a more preferable range is 0.85 mass% or more and 1.6 mass% or less.
Ｆｅの含有は、第二相分散粒子をＡｌ−Ｆｅ−Ｍｎ−Ｓｉ系金属間化合物とし、ろう付によって分散粒子がマトリックス相に再固溶して導電率（熱伝導性）が低下するのを防ぐことがさらなる目的である。Ｆｅの含有量が０．１０ｍａｓｓ％以下ではこの効果が得られない。同時に、本来フィン材はチューブ材に対する犠牲陽極材であるが、薄肉化したフィン材では、ある程度自己耐食性が良好でないと熱交換器において早期にフィン材が腐食により消失し、問題となることがある。０．７ｍａｓｓ％を超えるとＡｌ−Ｆｅ−Ｓｉ系の金属間化合物の割合が増し、フィン材の自己耐食性が低下するため、本発明では、Ｆｅの含有量は０．７ｍａｓｓ％未満の範囲である。上記理由からＦｅ含有量のより好ましい範囲は０．２ｍａｓｓ％以上０．６ｍａｓｓ％未満である。 The content of Fe is such that the second phase dispersed particles are made of an Al—Fe—Mn—Si intermetallic compound, and the dispersed particles are re-dissolved in the matrix phase by brazing and the conductivity (thermal conductivity) is lowered. It is a further purpose to prevent. This effect cannot be obtained when the Fe content is 0.10 mass% or less. At the same time, the fin material is originally a sacrificial anode material for the tube material, but if the fin material is thin, if the self-corrosion resistance is not good to some extent, the fin material may disappear due to corrosion at an early stage in the heat exchanger, which may be a problem. . If it exceeds 0.7 mass%, the proportion of Al-Fe-Si intermetallic compounds increases and the self-corrosion resistance of the fin material decreases, so in the present invention, the Fe content is in the range of less than 0.7 mass%. . For the above reason, the more preferable range of the Fe content is 0.2 mass% or more and less than 0.6 mass%.
また、本発明のフィン材を構成するＡｌ合金には、前記の必須元素に加え、犠牲陽極効果を有する亜鉛（Ｚｎ）、インジウム（Ｉｎ）、スズ（Ｓｎ）のうちの１種または２種以上、または／および強度向上に有効な銅（Ｃｕ）、チタン（Ｔｉ）、ジルコニウム（Ｚｒ）のうちの１種または２種以上を加えても良い。Ｚｎ，Ｉｎ，Ｓｎの添加は、犠牲陽極効果の付与とともに、フィン材自身の自己耐食性が劣化するので、それぞれの含有量の上限値は好ましくはＺｎ；３．０ｍａｓｓ％，Ｉｎ；０．３ｍａｓｓ％，Ｓｎ；０．３ｍａｓｓ％である。また、上述の強化元素を多量に加えると、Ｃｕ，Ｔｉの場合にはろう付後のフィン材の熱伝導性や、耐食性、犠牲陽極効果が、Ｚｒの場合には圧延性、疲労特性が低下するので、これらの元素を加える場合の好ましい含有量の上限はそれぞれ、Ｃｕ；０．２５ｍａｓｓ％，Ｔｉ；０．１ｍａｓｓ％，Ｚｒ；０．１ｍａｓｓ％である。
上述の元素の他に、化合物をさらに微細化する元素（例えばニッケル（Ｎｉ）、クロム（Ｃｒ）、コバルト（Ｃｏ））を本発明のフィン材に加えても構わない。その場合には、フィン材の耐食性、結晶組織制御の観点から好ましい含有量の上限はそれぞれ０．２ｍａｓｓ％である。
本発明のフィン材に用いられるアルミニウム合金の組成は、上述の元素の他、残部Ａｌおよび不可避不純物から成るものである。
The Al alloy constituting the fin material of the present invention includes one or more of zinc (Zn), indium (In), and tin (Sn) having a sacrificial anode effect in addition to the essential elements described above. Alternatively, and / or one or more of copper (Cu), titanium (Ti), and zirconium (Zr) effective for strength improvement may be added. Addition of Zn, In and Sn, together with the provision of the sacrificial anode effect, deteriorates the self-corrosion resistance of the fin material itself. Therefore, the upper limit value of each content is preferably Zn: 3.0 mass%, In: 0.3 mass% , Sn; 0.3 mass%. In addition, when Cu or Ti is added in a large amount, the heat conductivity, corrosion resistance, and sacrificial anode effect of the fin material after brazing are reduced in the case of Cu and Ti, and the rollability and fatigue characteristics are reduced in the case of Zr. Therefore, the upper limit of the preferable content when these elements are added is Cu: 0.25 mass%, Ti: 0.1 mass%, Zr: 0.1 mass%, respectively.
In addition to the elements described above, elements that further refine the compound (for example, nickel (Ni), chromium (Cr), cobalt (Co)) may be added to the fin material of the present invention. In that case, the upper limit of the preferable content from the viewpoint of the corrosion resistance of the fin material and the control of the crystal structure is 0.2 mass%.
The composition of the aluminum alloy used for the fin material of the present invention is composed of the balance of Al and inevitable impurities in addition to the above-mentioned elements.
次に本発明において、最後に行う中間焼鈍後の結晶組織を規定した理由を説明する。本発明は高強度フィンを主な対象にしているため、中間焼鈍によって再結晶させることが必須である。再結晶させてＯ材にせずとも０．１ｍｍ以下の板厚で、冷間圧延や、レベリング、スリッティングが容易に行える材料、例えばフィン材素材強度が１７０ＭＰａ以下のようなフィン材では本発明の製造方法を適用せずとも、容易にフィン材を製造できる。これに対して、本発明は中間焼鈍によって軟化させないと、素材強度が１７０ＭＰａ以上となって製造が困難となるような高強度フィン材に好適なものである。 Next, the reason why the crystal structure after the final annealing performed in the present invention is specified will be described. Since the present invention is mainly intended for high-strength fins, it is essential to recrystallize by intermediate annealing. A material having a thickness of 0.1 mm or less without being recrystallized to easily perform cold rolling, leveling, and slitting, for example, a fin material having a fin material strength of 170 MPa or less is used in the present invention. The fin material can be easily manufactured without applying the manufacturing method. On the other hand, the present invention is suitable for a high-strength fin material that has a material strength of 170 MPa or more and is difficult to manufacture unless softened by intermediate annealing.
本発明で規定される組成をもつアルミニウム合金には、微細な金属間化合物が密に分散しているため、中間焼鈍後の再結晶粒径は粗大化する。本発明における結晶組織に関する規定は、本発明者らが種々の結晶粒径を持つフィン材を観察した結果得た知見に基づいている。すなわち、圧延方向に１０ｍｍ未満の長さを持つ粗大な再結晶組織では、各結晶方位によって強度が異なるため、条材のフラットネスが保てず、冷間圧延率の制御やレベリング、スリッティングライン通板が困難になる。フラットネスを保つには、表面積の約８０％以上がこのように、繊維組織に近い粗大展伸組織、例えば略楕円形状の再結晶粒を有する必要がある。
本発明においては、最後の中間焼鈍後の圧延材の表層からみた表面積の８０％以上を占める再結晶粒の径の長さは、圧延材表面における圧延方向で、１０ｍｍ以上、好ましくは１０〜８０ｍｍ、さらに好ましくは１０〜４０ｍｍである。この圧延材を得るためには、例えば、上記組成のＡｌ合金を双ロール連続鋳造圧延法により、鋳造速度５００〜３００ｍｍ／ｍｉｎで、板厚２〜９ｍｍの板状鋳塊に作製し、通常の冷間圧延の条件で板厚０．１ｍｍ以下に圧延して、３００〜４８０℃、３０〜１５０分の最後の中間焼鈍を行なえばよい。中間焼鈍の温度が低すぎると十分に強度が低下しないため、得られるフィン材の成形性に劣り、また、高すぎると析出粒子が粗大化し、得られるフィン材のろう付加熱後の強度が低下する。
なお、本発明で、「表層から見た表面積」とは、板厚方向と垂直な面（ＬＴ−ＳＴ面）から目視で見たときの表面積をいい、その際の圧延材の大きさ（長さおよび幅）はいくつでも良い。スリッターを施した製品条幅でも、スリッター前の圧延全幅でも構わない。測定の便利上、製品条幅が好ましいが、どの大きさで測定しようとも結果は同じである。
In the aluminum alloy having the composition defined in the present invention, fine intermetallic compounds are densely dispersed, so that the recrystallized grain size after the intermediate annealing becomes coarse. The provisions relating to the crystal structure in the present invention are based on the knowledge obtained by the present inventors as a result of observing fin materials having various crystal grain sizes. That is, in a coarse recrystallized structure having a length of less than 10 mm in the rolling direction, the strength differs depending on each crystal orientation, so the flatness of the strip cannot be maintained, and control of the cold rolling rate, leveling, slitting line, etc. Threading becomes difficult. In order to maintain flatness, it is necessary that about 80% or more of the surface area has a coarse extended structure close to the fiber structure, for example, a substantially elliptical recrystallized grain.
In the present invention, the length of the diameter of the recrystallized grains occupying 80% or more of the surface area as viewed from the surface layer of the rolled material after the final intermediate annealing is 10 mm or more, preferably 10 to 80 mm in the rolling direction on the surface of the rolled material. More preferably, it is 10-40 mm. In order to obtain this rolled material, for example, an Al alloy having the above composition is produced into a plate-shaped ingot having a thickness of 2 to 9 mm at a casting speed of 500 to 300 mm / min by a twin roll continuous casting and rolling method. Rolling to a sheet thickness of 0.1 mm or less under the conditions of cold rolling, the final intermediate annealing at 300 to 480 ° C. for 30 to 150 minutes may be performed. If the temperature of the intermediate annealing is too low, the strength is not sufficiently reduced, so the moldability of the resulting fin material is inferior, and if it is too high, the precipitated particles become coarse, and the strength of the obtained fin material after brazing heat decreases. To do.
In the present invention, the “surface area viewed from the surface layer” refers to the surface area as viewed from the surface perpendicular to the plate thickness direction (LT-ST surface), and the size (long) of the rolled material at that time The width and width) can be any number. It may be the product width subjected to slitting, or the entire rolling width before slitting. For convenience of measurement, the product width is preferable, but the result is the same regardless of the size.
フィン材を再結晶させる最後の中間焼鈍を、板厚０．１ｍｍ以下で行なうことに限定したのは、これ以上の板厚で焼鈍を行った場合、本発明の他の要件を満たしても、０．１ｍｍ以下、例えば０．０６ｍｍの最終板厚まで圧延すると相当量のひずみが蓄えられ、ろう付加熱の際の再結晶組織が微細になってろう材のエロージョン（浸食）が生じやすくなるためである。また、多量のひずみが蓄えられた高強度フィン材は、素材強度が高くなりコバ割れなどの不良が生じる。本発明は、最終冷間圧延率が低く、耐ろう材エロージョン性と生産性に優れたフィン材を製造することを目的とするので、最後の中間焼鈍は最終板厚に近い板厚で行う。本発明においてアルミニウム合金は、最後の中間焼鈍を行ったのち冷間圧延によってブレージング用フィン材に製造するが、その際の冷間圧延率を３０％未満に規定した理由も、同様にろう付時のエロージョンと、圧延時のコバ割れを防ぐためである。最後の中間焼鈍後の冷間圧延における板厚圧下率（冷間圧延率）は１２〜２８％であることが好ましい。 The final intermediate annealing for recrystallizing the fin material is limited to be performed at a plate thickness of 0.1 mm or less, and when annealing is performed at a plate thickness of more than this, even if the other requirements of the present invention are satisfied, When rolling to a final thickness of 0.1 mm or less, for example 0.06 mm, a considerable amount of strain is accumulated, and the recrystallized structure becomes finer during brazing heat addition, and erosion of the brazing material is likely to occur. It is. In addition, a high-strength fin material in which a large amount of strain is stored has a high material strength and causes defects such as edge cracks. The object of the present invention is to produce a fin material having a low final cold rolling rate and excellent brazing material erosion resistance and productivity, so that the final intermediate annealing is performed with a plate thickness close to the final plate thickness. In the present invention, the aluminum alloy is manufactured into a brazing fin material by cold rolling after the final intermediate annealing. The reason for defining the cold rolling rate at less than 30% at that time is also the same as that during brazing. This is to prevent erosion and cracking during rolling. The sheet thickness reduction ratio (cold rolling ratio) in the cold rolling after the final intermediate annealing is preferably 12 to 28%.
中間焼鈍後のフィン材の結晶組織を観察するには、得られた合金フィン材を王水中に浸漬し、板材表面を直接観察すれば良い。本発明のような粗大な結晶組織を観察するには目視で十分である。圧延方向に粗大である結晶粒は、通常、板厚方向に１〜２個の結晶粒しか有さないため、表層からの観察を行えば良い。本発明において、表層から見た表面積の圧延方向に長さ１０ｍｍ以上の径を有する再結晶粒が占める割合は８０％以上であり、８５％以上が好ましい。中間焼鈍後のサンプルを採取出来ない場合には、フィン製品を観察しても良い。なぜならば中間焼鈍で粗大な結晶組織になっている場合、その後本発明の規定範囲のような低い圧延率で圧延した後の結晶組織もほぼ同等なためである。 In order to observe the crystal structure of the fin material after the intermediate annealing, the obtained alloy fin material may be immersed in aqua regia and the plate material surface may be directly observed. Visual observation is sufficient to observe a coarse crystal structure as in the present invention. The crystal grains that are coarse in the rolling direction usually have only one or two crystal grains in the plate thickness direction, and therefore observation from the surface layer may be performed. In the present invention, the proportion of recrystallized grains having a diameter of 10 mm or more in the rolling direction of the surface area viewed from the surface layer is 80% or more, preferably 85% or more. If the sample after the intermediate annealing cannot be collected, the fin product may be observed. This is because when a coarse crystal structure is formed by intermediate annealing, the crystal structure after rolling at a low rolling rate as in the specified range of the present invention is almost the same.
さらに、ろう付後の再結晶組織から加熱前の再結晶組織を推定することも可能である。ろう付加熱後の再結晶粒径が本発明のように粗大であるためには、通常のろう付加熱条件（約６００℃×数分）を鑑みると、加熱前の結晶組織は繊維組織か、粗大再結晶組織のどちらかに限定できる。微細な再結晶組織をろう付加熱しても１０ｍｍ以上に成長するほどろう付による加熱時間は長くはない。また、繊維組織から再結晶した組織と、粗大再結晶組織から再結晶した組織では、結晶粒界の形状が異なる。すなわち図１、２のろう付け加熱前後におけるフィン材結晶組織の写真に示すように粗大再結晶組織から再結晶した結晶粒界（図１：参考例１）は、繊維組織からのそれ（図２：参考例２）と比較し、鋸歯状になる。これは繊維組織からの再結晶する場合と異なり、一度再結晶することにより歪みが低減したことによって再結晶の駆動力が小さくなっており、さらに中間焼鈍温度が高いため析出が進み、粒界の移動を妨げる分散粒子が多いためである。このような違いに注目すると、ろう付後の再結晶組織から、加熱前の再結晶組織が推定でき、さらに中間焼鈍温度直後の再結晶組織を推測できる。
なお、図１、２において、各上段はろう付け前、各下段はろう付け後を示し、スケールの最小目盛りは図１では１ｍｍ、図２では０．５ｍｍである。また、再結晶粒サイズは、長径（圧延方向。図中左右方向）で測定したものである。図２では、上段に示すろう付け前の完全繊維状組織から下段に示すろう付け後の再結晶組織へ再結晶し、結晶粒の形状が大きく変化する。これに対して、図１では、上段に示すろう付け前の再結晶組織は、下段に示すろう付け後の図では圧延方向に若干展進して、異方性の特徴が弱くなっており、結晶組織の短径（巾方向。図中上下方向）が太くなり、再結晶が生じているが、鋸歯状の形状の結晶粒界を維持している。すなわち、ろう付け後において、図１に示されるような再結晶組織（圧延方向に長さ１０ｍｍ以上の径を有する粗大な鋸歯状の再結晶粒が表面積の８０％以上を占める組織）であれば、中間焼鈍後の再結晶組織が本発明で規定する再結晶組織であることが推測できる。
本発明においては、上記で説明された条件以外は、適宜常法を用いてフィン材を製造することができる。
Furthermore, it is possible to estimate the recrystallized structure before heating from the recrystallized structure after brazing. In order for the recrystallized grain size after brazing heat to be coarse as in the present invention, in view of normal brazing heat treatment conditions (about 600 ° C. × several minutes), the crystal structure before heating is a fiber structure, It can be limited to either a coarse recrystallized structure. Even if a fine recrystallized structure is heated by brazing, the heating time by brazing is not so long that it grows to 10 mm or more. Moreover, the shape of the crystal grain boundary differs between the structure recrystallized from the fiber structure and the structure recrystallized from the coarse recrystallized structure. That is, as shown in the photographs of the crystal structure of the fin material before and after brazing heating in FIGS. 1 and 2, the grain boundaries recrystallized from the coarse recrystallized structure (FIG. 1 : Reference Example 1 ) are those from the fiber structure (FIG. 2). : Compared with Reference Example 2 ), it has a sawtooth shape. This is different from the case of recrystallization from the fiber structure, and the recrystallization driving force is reduced due to the reduction of strain by recrystallization once, and further the precipitation proceeds due to the high intermediate annealing temperature. This is because there are many dispersed particles that hinder movement. Paying attention to such a difference, the recrystallized structure before heating can be estimated from the recrystallized structure after brazing, and the recrystallized structure immediately after the intermediate annealing temperature can be estimated.
In FIG. 1, 2, each upper stage before brazing, each lower indicates after brazing, the minimum scale of the scale in FIG. 1 1 mm, a 0.5mm in FIG. Further, the recrystallized grain size is measured by a major axis (rolling direction, left and right direction in the figure). In FIG. 2 , it recrystallizes from the complete fibrous structure before brazing shown in the upper stage to the recrystallized structure after brazing shown in the lower stage, and the shape of the crystal grains changes greatly. In contrast, in the FIG. 1, before brazing recrystallized structure shown in the upper part, in the drawing after brazing as shown in the lower part with slightly TenSusumu in the rolling direction, and characteristics of the anisotropic weakens The minor axis (width direction; vertical direction in the figure) of the crystal structure becomes thick and recrystallization occurs, but the crystal grain boundary in a sawtooth shape is maintained. That is, after brazing, if it is a recrystallized structure as shown in FIG. 1 (a structure in which coarse sawtooth recrystallized grains having a diameter of 10 mm or more in the rolling direction occupy 80% or more of the surface area) It can be presumed that the recrystallized structure after the intermediate annealing is the recrystallized structure defined in the present invention.
In the present invention, except for the conditions described above, the fin material can be appropriately produced using a conventional method.
以上説明したように、本発明規定のアルミニウム合金から製造されるフィン材は、ろう付後の特性、特に強度とろう付加熱中の耐ろう拡散性に優れる。また、フィン材に製造する際の薄肉における冷間圧延性、レベリング、スリッティングなどが問題なく製造できるものである。 As described above, the fin material produced from the aluminum alloy defined in the present invention is excellent in characteristics after brazing, particularly strength and resistance to brazing diffusion during brazing heat. Moreover, the cold rolling property, leveling, slitting, etc. in the thin wall when manufacturing into the fin material can be manufactured without problems.
以下に本発明を実施例により詳細に述べる。
実施例
（本発明例）
表１に示す本発明規定組成のＡｌ合金Ｎｏ．１を溶解し、得られる溶湯をロール径８８０ｍｍの双ロールを用いた連続鋳造圧延法により、溶湯の冷却速度１０００ｍｍ／ｍｉｎで幅１０００ｍｍの板状鋳塊に鋳造して、コイル状に巻き取り、板厚０．１ｍｍ以下で、４００℃、１２０分間の最後の中間焼鈍を行なった。中間焼鈍後、後述のマクロ観察により、表層からみた再結晶粒の圧延方向の径の長さの最大のものは１８ｍｍであり、１０ｍｍ以上の再結晶粒は、表面積の約９０％を占めていた。次いでこれを板厚圧下率２０％で冷間圧延して本発明例１のフィン材を製造した。同様にして、表１に示す本発明規定組成のＡｌ合金Ｎｏ．２〜５を用いて、それぞれ本発明例２〜５のフィン材を製造した。
The present invention will be described in detail below with reference to examples.
Example (Invention Example)
The Al alloy no. 1 is melted, and the resulting molten metal is cast into a plate-shaped ingot having a width of 1000 mm at a cooling rate of 1000 mm / min by a continuous casting and rolling method using a twin roll having a roll diameter of 880 mm, and wound into a coil shape. The final intermediate annealing was performed at 400 ° C. for 120 minutes with a plate thickness of 0.1 mm or less. After the intermediate annealing, the maximum length of the diameter in the rolling direction of the recrystallized grains as seen from the surface layer was 18 mm by macro observation described later, and the recrystallized grains of 10 mm or more occupied about 90% of the surface area. . Next, this was cold-rolled at a sheet thickness reduction of 20% to produce the fin material of Inventive Example 1. In the same manner, the Al alloy no. The fin materials of Invention Examples 2 to 5 were produced using 2 to 5, respectively.
（比較例）
表１に示す本発明規定外組成のＡｌ合金Ｎｏ．６〜１１を用いた他は、本発明例１〜５と同様にして、それぞれ比較例６〜１１のフィン材を製造した。
また、本発明規定組成である、表１中の合金Ｎｏ．１を用いたが、中間焼鈍を２８０℃で６００分間に変更した以外は、本発明例１〜５と同様にして比較例１２のフィン材を製造した。
(Comparative example)
Table 1 shows an Al alloy no. The fin material of Comparative Examples 6-11 was manufactured similarly to Example 1-5 of this invention except having used 6-11, respectively.
In addition, the alloy no. 1 was used, but the fin material of Comparative Example 12 was produced in the same manner as in Invention Examples 1 to 5 except that the intermediate annealing was changed to 280 ° C. for 600 minutes.
（試験例）
本発明例および比較例のフィン材について、冷間圧延中に破断したか否か、また、レベリングおよびスリッティング工程において通板出来なかった、或いは困難だったか否かを評価した。上記のような製造上の不具合によって工業的に製造出来なかったものについては、残部をラボ設備を用いてフィン材に冷間圧延して試験或いは評価した。これらの試験、評価結果を表２に示す。
表２で圧延中の破断の有無は、前記の冷間圧延中の破断の有無である。
また、最終の中間焼鈍後、および圧延完了後の結晶組織を、Ａｌ合金フィン材２００ｍｍ×２０ｍｍの表面を王水に浸漬することによりマクロエッチングして、マクロ組織を観察し、評価した。表２では、再結晶組織が、圧延方向に長さ１０ｍｍ以上の径の再結晶粒が表面積に対して８０％以上の場合には○、８０％未満６０％以上であった場合には△、６０％未満の場合は×で示した。なお、表面積中の１０ｍｍ以上の再結晶粒が占める割合は、マクロエッチングしたフィン材表面の写真を画像としてコンピュータに取り込み、画像解析ツールを用いて解析した。
また、以下の評価試験を行なった。それぞれの試験結果について表２に示した。
フィン材をろう付相当条件（６００℃×４分）で加熱したのち、引張強さ、および導電率を測定した。引張強さはＪＩＳ Ｚ ２２４１に準じ、導電率はＪＩＳ Ｈ ０５０５に準じてそれぞれ評価した。
ここで、導電率は熱伝導性の指標であり、フィンの導電率が５％ＩＡＣＳ向上すると、熱交換器の熱効率は１％程度向上する。
耐垂下性は、フィン材を突き出し長さが５０ｍｍとなるように水平に指示し、６００℃で１０分間加熱、加熱後の垂下量（ｍｍ）を測定し、評価した。自己耐食性は７日間のＣＡＳＳ試験を行ったのち重量減少率を調べて評価した。
また、コルゲート状に成形したフィン材を、長さ１００ｍｍのチューブ材に組み付け、ろう付けにより５段のミニコアを作製した。このミニコアについてフィン溶けの有無をミクロ観察により調べて評価した。フィン溶けの評価は、特開２００３−３４８５１号公報記載の内容と同等の基準で行った。
(Test example)
About the fin material of the example of the present invention and the comparative example, it was evaluated whether or not it broke during cold rolling, and whether or not it could not pass through in the leveling and slitting process. For those that could not be industrially manufactured due to the above manufacturing problems, the remainder was cold-rolled into a fin material using a laboratory facility and tested or evaluated. These tests and evaluation results are shown in Table 2.
In Table 2, the presence or absence of breakage during rolling is the presence or absence of breakage during the cold rolling.
Further, the crystal structure after the final intermediate annealing and after the completion of rolling was subjected to macro etching by immersing the surface of the Al alloy fin material 200 mm × 20 mm in aqua regia, and the macro structure was observed and evaluated. In Table 2, the recrystallized structure is ◯ when the recrystallized grain having a diameter of 10 mm or more in the rolling direction is 80% or more with respect to the surface area, and Δ when the recrystallized grain is less than 80% and 60% or more. When it was less than 60%, it was shown by x. The ratio of the recrystallized grains of 10 mm or more in the surface area was analyzed by using a macro-etched fin material surface image as an image in a computer and using an image analysis tool.
Moreover, the following evaluation tests were conducted. The test results are shown in Table 2.
The fin material was heated under brazing equivalent conditions (600 ° C. × 4 minutes), and then the tensile strength and conductivity were measured. The tensile strength was evaluated according to JIS Z 2241 and the electrical conductivity was evaluated according to JIS H 0505.
Here, the electrical conductivity is an index of thermal conductivity. When the electrical conductivity of the fin is improved by 5% IACS, the thermal efficiency of the heat exchanger is improved by about 1%.
The drooping resistance was evaluated by measuring the drooping amount (mm) after heating by heating at 600 ° C. for 10 minutes, instructing the fin material horizontally so that the length was 50 mm. The self-corrosion resistance was evaluated by examining the weight loss rate after conducting a CASS test for 7 days.
Moreover, the fin material shape | molded in corrugated form was assembled | attached to the tube material of length 100mm, and the 5-stage mini core was produced by brazing. This mini-core was evaluated by examining the presence or absence of fin melting by micro observation. Evaluation of fin melting was performed based on the same standards as described in JP-A-2003-34851.
表２から明らかなように、本発明例１〜５のフィン材はいずれも冷間圧延中に破断せず、また、レベリング、スリッティングラインも問題なく通板し、フィン材に製造することができた。フィン材は耐垂下性と自己耐食性に優れ、ろう付加熱後における引張強さと導電率が高く、コルゲート成形され、フィン溶けも生じなかった。 As is clear from Table 2, none of the fin materials of Invention Examples 1 to 5 breaks during cold rolling, and the leveling and slitting lines can be passed through without problems and manufactured into fin materials. did it. The fin material was excellent in drooping resistance and self-corrosion resistance, had high tensile strength and conductivity after brazing heat, was corrugated, and did not melt the fin.
一方、比較例６は、添加Ｍｎ量が多く、圧延中に破断した。残部から作製したフィン材は、ろう付相当加熱後の導電率が低下していた。
比較例７は、添加Ｍｎ量が少ないため、第二相分散粒子の大部分がＡｌ−Ｆｅ−Ｓｉ系金属間化合物となっていた。このため自己耐食性が低下した。また、Ａｌ−Ｆｅ−Ｓｉ系化合物は、Ａｌ−Ｆｅ−Ｍｎ−Ｓｉ系金属間化合物と比較して粗大であるため、再結晶の核生成サイトとなり、再結晶が微細となった。その結果、垂下量が増加し、フィン溶けが生じた。また、ろう付相当加熱後の引張強さが低下した。
比較例８は添加Ｓｉ量が多いために、ろう付時フィン溶けが生じた。また、初晶Ｓｉが生成したため、再結晶の核となりグレインサイズが微細化し、１０ｍｍ以下となった。これによりフラットネスが悪化し、レベリングを行えなかった。
比較例９はＳｉが少なく、Ａｌ−Ｆｅ−Ｍｎ系の晶出物が粗大化し、再結晶の核生成サイトとなった。従って中間焼鈍後のグレインサイズが圧延方向で４〜５ｍｍとなった。さらに、Ｓｉ量が不足したため、ろう付加熱後の引張強さが低下した。
比較例１０は添加Ｆｅ量が多いため、第二相分散粒子のうち、Ａｌ−Ｆｅ−Ｓｉ系金属間化合物の割合が増していた。このため自己耐食性が低下した。
比較例１１はＦｅ量が少なく、ＭｎとＳｉの晶析出量が減少したため、ろう付相当加熱後の引張強さと導電率が低下した。代わりに初晶Ｓｉが生成したため、再結晶の核となりグレインサイズが数百μｍに微細化した。初晶Ｓｉとグレインサイズによりフィン溶けが生じた。
比較例１２は、ろう付中、およびろう付加熱後のフィン特性は問題なかったが、レベリングおよびスリッティング工程においてフラットネスの悪化により通板が困難であった。
On the other hand, Comparative Example 6 had a large amount of added Mn and broke during rolling. The fin material produced from the remaining portion had a reduced electrical conductivity after brazing equivalent heating.
In Comparative Example 7, since the amount of added Mn was small, most of the second phase dispersed particles were Al—Fe—Si intermetallic compounds. For this reason, self-corrosion resistance fell. Further, since the Al—Fe—Si-based compound is coarser than the Al—Fe—Mn—Si-based intermetallic compound, it becomes a nucleation site for recrystallization and recrystallization becomes fine. As a result, the amount of drooping increased and fin melting occurred. Moreover, the tensile strength after brazing equivalent heating fell.
In Comparative Example 8, since the amount of added Si was large, fin melting occurred during brazing. Further, since primary crystal Si was formed, it became the nucleus of recrystallization and the grain size was refined to 10 mm or less. As a result, flatness deteriorated and leveling could not be performed.
In Comparative Example 9, the amount of Si was small, and the Al-Fe-Mn-based crystallized material became coarse and became a nucleation site for recrystallization. Therefore, the grain size after the intermediate annealing was 4 to 5 mm in the rolling direction. Furthermore, since the amount of Si was insufficient, the tensile strength after brazing addition heat decreased.
In Comparative Example 10, since the amount of added Fe was large, the proportion of the Al—Fe—Si intermetallic compound in the second phase dispersed particles increased. For this reason, self-corrosion resistance fell.
In Comparative Example 11, the amount of Fe was small and the amount of crystal precipitation of Mn and Si was reduced, so that the tensile strength and conductivity after brazing equivalent heating were lowered. Instead, primary crystal Si was formed, which became the core of recrystallization and the grain size was refined to several hundred μm. Fin melting occurred due to primary crystal Si and grain size.
In Comparative Example 12, there was no problem with fin characteristics during brazing and after brazing addition heat, but it was difficult to pass the plate due to deterioration of flatness in the leveling and slitting processes.
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