JP2013204078A - Aluminum alloy clad material for heat exchanger - Google Patents
Aluminum alloy clad material for heat exchanger Download PDFInfo
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- JP2013204078A JP2013204078A JP2012073164A JP2012073164A JP2013204078A JP 2013204078 A JP2013204078 A JP 2013204078A JP 2012073164 A JP2012073164 A JP 2012073164A JP 2012073164 A JP2012073164 A JP 2012073164A JP 2013204078 A JP2013204078 A JP 2013204078A
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Abstract
Description
本発明は、強度と耐久性に優れる熱交換器用アルミニウム合金クラッド材に関する。 The present invention relates to an aluminum alloy clad material for a heat exchanger that is excellent in strength and durability.
近年、自動車等のアルミニウム合金製熱交換器は性能向上のため、内圧が高まる傾向があり、そのため各部材への負荷が増大し、耐久性が低下する問題が発生している。これまでの使用環境では各部材は塑性変形を伴わない弾性域内で使用されていたため、材料の高強度化によって耐久性の向上を図っていたが、近年は特に薄肉材において局部的に塑性変形を伴う低サイクル疲労領域で使用される場合もあり、そのような使用環境においては材料を高強度化すると耐久性を低下させることになりかねない。したがって、高サイクル疲労域から低サイクル疲労域の広い範囲において優れた耐久性の確保が可能な材料が求められている。 In recent years, aluminum alloy heat exchangers such as automobiles have a tendency to increase internal pressure in order to improve performance. Therefore, there is a problem that the load on each member increases and durability decreases. In the conventional usage environment, each member has been used in an elastic range that does not cause plastic deformation, so the durability has been improved by increasing the strength of the material. In some cases, it is used in a low cycle fatigue region, and in such a use environment, if the strength of the material is increased, the durability may be lowered. Therefore, there is a demand for a material capable of ensuring excellent durability in a wide range from a high cycle fatigue region to a low cycle fatigue region.
自動車等の熱交換器には、Ａｌ-Ｍｎ-Ｃｕ系合金からなる芯材の片面または両面にＡｌ-Ｓｉ系ろう材が貼り合せされたブレージングシートやろう材の他方の片面に犠牲陽極材としてＡｌ-Ｚｎ系合金が貼り合せされたアルミニウム合金クラッド材が使用されている。
芯材には強度や成形性、ろう付け性に優れるＡｌ-Ｍｎ-Ｃｕ系合金が一般的に使用されており、熱交換器の構造部材として形状を保持する効果を有している。また、熱交換器として使用時の内圧変動や振動、温度変化に起因する熱応力によって発生する疲労に対する耐久性を向上する効果がある。
Ａｌ-Ｓｉ系のろう材はチューブとフィン、チューブとヘッダープレートなどのろう付け接合のために貼り合わされており、通常、不活性ガス雰囲気中でフッ化物フラックスを用いて約６００℃程度のろう付け熱処理で接合が行われる。犠牲陽極材は冷媒の流路となるチューブ材の内面や外面などに配置され、熱交換器の使用中に作動流体や外気に対して犠牲陽極効果を発揮し、芯材への腐食進行による冷却水等の洩れを抑制する効果を有する。通常、アウターフィンやインナーフィンにはベア材が使用され、チューブやプレート部材から供給されるろう材によって接合が行われる。
自動車など輸送機器の熱交換器は軽量化のため、部材の薄肉化が進展してきており、耐久性向上のため部材の高強度化が図られてきた。部材の高強度化は芯材のＣｕ,Ｓｉ,Ｍｎの添加量の増加や犠牲材へのＭｇ添加によって実現されている(例えば、特許文献１)。
For heat exchangers such as automobiles, a brazing sheet in which an Al—Si brazing material is bonded to one or both sides of a core material made of an Al—Mn—Cu alloy or a sacrificial anode material on the other side of the brazing material An aluminum alloy clad material bonded with an Al—Zn alloy is used.
An Al—Mn—Cu alloy having excellent strength, formability and brazing is generally used for the core material, and has an effect of maintaining the shape as a structural member of the heat exchanger. In addition, there is an effect of improving durability against fatigue caused by thermal stress caused by internal pressure fluctuation, vibration, and temperature change during use as a heat exchanger.
Al-Si brazing materials are bonded together for brazing joints such as tubes and fins, tubes and header plates, and are usually brazed at about 600 ° C using a fluoride flux in an inert gas atmosphere. Joining is performed by heat treatment. The sacrificial anode material is arranged on the inner and outer surfaces of the tube material that serves as the refrigerant flow path, and exhibits a sacrificial anode effect on the working fluid and outside air during use of the heat exchanger, and cooling due to the progress of corrosion to the core material It has the effect of suppressing leakage of water and the like. Usually, a bare material is used for the outer fin and the inner fin, and the joining is performed by a brazing material supplied from a tube or a plate member.
Heat exchangers for transportation equipment such as automobiles have been made thinner in order to reduce the weight, and the strength of the members has been increased in order to improve durability. Strengthening of the member is realized by increasing the amount of Cu, Si, Mn added to the core material or adding Mg to the sacrificial material (for example, Patent Document 1).
しかし、近年は部材の薄肉化がますます進展し、さらには熱交換性能向上のために内圧が高い環境で使用される熱交換器も増加しており、従来品に比べ、チューブやフィンなど薄肉部材の耐久性が著しく低下する問題が発生している。特にチューブに板厚０.２ｍｍ以下の薄肉部材が使用されるラジエータや内圧が高い環境で使用されるオイルクーラ、１００℃以上の高温で使用されるインタークーラなどの各種熱交換器で耐久性の低下が問題となっており、そのような使用環境においても疲労特性に優れる材料が強く望まれている。
また、薄肉のチューブ材等においては芯材を高強度化するとろう付け時の元素拡散により、ろう付け後に芯材と表層材の電位差が低下し、耐食性が確保できずに早期に貫通孔が発生する問題が生じる。また、フィン材ではＺｎ添加量を増加するとチューブ等に対する犠牲陽極効果は向上するが、腐食速度が増大するため腐食によってフィン材の板厚を貫通するような腐食部位が多数発生し、構造強度の低下により短期間で耐久性が低下する場合もある。
以上のように、近年、熱交換器はさらなる軽量化、高性能化を実現するため、熱交換器用部材には優れた耐久性と耐食性の両立が求められている。
本発明は、このような課題に基づいてなされたもので、薄肉化されても、内圧の高い環境で疲労特性及び耐食性に優れる熱交換器用アルミニウムクラッド材を提供することを目的とする。
However, in recent years, the thickness of components has been further reduced, and heat exchangers used in environments with high internal pressure have been increasing to improve heat exchange performance. There has been a problem that the durability of the member is significantly reduced. Particularly durable in various heat exchangers such as radiators that use thin members with a thickness of 0.2 mm or less for tubes, oil coolers that are used in environments with high internal pressure, and intercoolers that are used at high temperatures of 100 ° C or higher. Deterioration is a problem, and a material excellent in fatigue characteristics even in such a use environment is strongly desired.
In addition, in thin-walled tube materials, etc., if the core material is strengthened, elemental diffusion during brazing will reduce the potential difference between the core material and the surface layer material after brazing, and corrosion resistance cannot be ensured, resulting in early through holes. Problems arise. In addition, when the Zn content is increased in the fin material, the sacrificial anode effect on the tube and the like is improved, but since the corrosion rate is increased, many corrosion sites that penetrate the plate thickness of the fin material are generated due to corrosion, and the structural strength is increased. The durability may decrease in a short period due to the decrease.
As described above, in recent years, heat exchangers are required to have both excellent durability and corrosion resistance in order to realize further weight reduction and high performance.
The present invention has been made based on such a problem, and an object of the present invention is to provide an aluminum clad material for a heat exchanger that is excellent in fatigue characteristics and corrosion resistance in an environment having a high internal pressure even when the thickness is reduced.
本発明者は、上述した使用環境においても耐久性に優れる材料を得るため、熱交換器使用時に各部材へ負荷される応力や歪みを計測し、最適なクラッド構成について検討を行なった。その結果、従来は薄肉部材であっても、ほとんど塑性変形を伴わない弾性域内の高サイクル疲労域にて使用されていたが、耐久性の著しい低下が見られた熱交換器では局所的に塑性変形が発生する低サイクル疲労域となっており、そのような使用環境において高強度材を適用すると、かえって耐久性が低下することが確認された。 In order to obtain a material having excellent durability even in the use environment described above, the present inventor has measured the stress and strain applied to each member when using the heat exchanger, and studied the optimum clad configuration. As a result, even thin-walled members have been used in the high-cycle fatigue region within the elastic region with almost no plastic deformation. It is a low cycle fatigue region where deformation occurs, and it has been confirmed that when a high strength material is applied in such a use environment, the durability is rather lowered.
一般的に、高サイクル疲労には高い強度を有する材料、低サイクル疲労には高い伸びを有する材料が耐久性に優れるが、強度と伸びは通常相反する特性となるため、その両立は困難である。そこで、発明者らはクラッド材を構成する芯材成分と表面に貼り合せるアルミニウム層の組合せについて鋭意検討した結果、不可避不純物量を抑制した低強度のＡｌ-Ｚｎ合金を応力緩和層として表層材を設けることで、芯材への疲労亀裂の進展が抑制され、著しく耐久性が向上することを知見した。 In general, materials with high strength for high cycle fatigue and materials with high elongation for low cycle fatigue are excellent in durability, but both strength and elongation are usually contradictory properties, making it difficult to achieve both . Therefore, as a result of intensive studies on the combination of the core component constituting the clad material and the aluminum layer to be bonded to the surface, the inventors have determined that the surface layer material is made of a low-strength Al-Zn alloy with a reduced amount of inevitable impurities as a stress relaxation layer. It has been found that, by providing, the progress of fatigue cracks in the core material is suppressed and the durability is remarkably improved.
本発明はこの知見に基づいており、質量％で、Ｍｎ:０.５〜２.０％、Ｃｕ：０.１〜１.０％、Ｓｉ：０.３〜１.０％、Ｆｅ：０.１〜１.０％を含有し、残部がＡｌと不可避不純物からなる組成のアルミニウム合金芯材の片面または両面にろう付け熱処理後の耐力が３０ＭＰａ以下のＡｌ-Ｚｎ合金が貼り合わされ、前記Ａｌ-Ｚｎ合金は質量％で、Ｚｎ：０.５〜５.０％を含有し、残部が不可避不純物からなり、不可避不純物中のうちＣｕ,Ｍｇの含有量がいずれも０.０５％未満であることを特徴とする熱交換器用アルミニウム合金クラッド材である。
本発明によるクラッド材は、芯材にＺｎ:０.１〜３.０％及びＭｇ：０.０１〜１.０％の１種又は２種を含有させることができる。
The present invention is based on this finding, and in terms of mass%, Mn: 0.5 to 2.0%, Cu: 0.1 to 1.0%, Si: 0.3 to 1.0%, Fe: 0 Al-Zn alloy having a proof stress of 30 MPa or less after brazing heat treatment is bonded to one side or both sides of an aluminum alloy core material containing 0.1 to 1.0%, the balance being Al and inevitable impurities, -Zn alloy is mass%, contains Zn: 0.5-5.0%, the remainder consists of inevitable impurities, and the contents of Cu and Mg in the inevitable impurities are both less than 0.05% This is an aluminum alloy clad material for a heat exchanger.
The clad material according to the present invention may contain one or two of Zn: 0.1 to 3.0% and Mg: 0.01 to 1.0% in the core material.
本発明のクラッド材は、芯材の片方の面にのみ表層材が貼り合わされる形態の他に、芯材の片方の面に表層材が貼り合わされ、芯材の他方の面に質量％でＳｉ：５.０〜１２.０％を含むろう材層が貼り合わされる形態に適用できる。 In the clad material of the present invention, the surface layer material is bonded to only one surface of the core material, the surface layer material is bonded to one surface of the core material, and the other surface of the core material is Si in mass%. : Applicable to a form in which a brazing filler metal layer containing 5.0 to 12.0% is bonded.
また本発明のクラッド材において、表層材のろう付け熱処理後の表面ビッカース硬さが３５Ｈｖ以下であることが好ましい。 In the clad material of the present invention, the surface Vickers hardness after brazing heat treatment of the surface layer material is preferably 35 Hv or less.
本発明の熱交換器用アルミニウムクラッド材は、薄肉化されても、内圧の高い環境において優れた疲労特性を発揮する。さらに本発明のクラッド材は、長期間にわたる耐食性をも兼ね備える。 Even if the aluminum clad material for heat exchangers of the present invention is thinned, it exhibits excellent fatigue characteristics in an environment with a high internal pressure. Furthermore, the clad material of the present invention also has long-term corrosion resistance.
熱交換器の構造強度や高サイクル疲労域の耐久性を確保するため、特に板厚が薄い場合には芯材にはなるべく強度の高い合金を使用し、熱交換器使用時に最も負荷応力が高くなる表層部に低強度で延性に富む表層材を配置したクラッド材とすることにより、本発明のクラッド材は、高サイクル疲労域から低サイクル疲労域の広範囲において優れた耐久性を得る。また、表層材に電位の低いＡｌ-Ｚｎ合金を使用することで、犠牲陽極効果により耐食性も向上し、厳しい腐食環境での使用においても、長期に渡り、優れた耐久性を維持できる。
本発明によるクラッド材は、チューブやプレートなどの各部材に適用しても同様に疲労特性の向上効果を得ることができるが、特に熱交換器としての使用時に塑性変形が発生しやすい板厚が１ｍｍ以下の部材に適用すると劇的な効果が得られる。なお、板材としての下限は、０．０３ｍｍである。
In order to ensure the structural strength of the heat exchanger and durability in the high cycle fatigue region, use an alloy with the highest possible strength as the core material, especially when the plate thickness is thin, and the highest load stress when using the heat exchanger By using a clad material in which a surface layer material having low strength and high ductility is disposed on the surface layer portion, the clad material of the present invention has excellent durability in a wide range from a high cycle fatigue region to a low cycle fatigue region. Further, by using an Al—Zn alloy having a low electric potential as the surface layer material, the corrosion resistance is improved by the sacrificial anode effect, and excellent durability can be maintained for a long time even in use in a severe corrosive environment.
The clad material according to the present invention can obtain the effect of improving fatigue characteristics in the same manner even when applied to each member such as a tube and a plate. When applied to a member of 1 mm or less, a dramatic effect can be obtained. In addition, the minimum as a board | plate material is 0.03 mm.
熱交換器では薄肉のフィン材が最初に破断し、その後チューブ等の変形量が増大し、疲労クラックの進展により、破壊に至る場合が多く、本発明材をアウターフィンやインナーフィンとして使用するとその効果が大きく、最も好適である。通常これらのフィン材はベア材で使用されるが、表層に強度の低い材料を貼り合せた本発明のクラッド材の使用によって著しい耐久性の向上が図れる。
もちろん、本発明によるクラッド材をプレート、チューブなどの各部材に適用しても同様に疲労特性の向上効果を得ることができる。
以上のように、クラッド材の芯材成分と表層材の成分や物性ならびにその組合せを最適化することで、従来材を使用した場合に比べ、熱交換器の耐久性と耐食性を飛躍的に向上することが可能となるのである。
In a heat exchanger, the thin fin material is first broken, then the amount of deformation of the tube and the like is increased, and fatigue cracks often lead to breakage.When the present invention material is used as an outer fin or inner fin, The effect is great and most suitable. Usually, these fin materials are used as bare materials, but the durability can be significantly improved by using the clad material of the present invention in which a low-strength material is bonded to the surface layer.
Of course, even if the clad material according to the present invention is applied to each member such as a plate and a tube, the effect of improving the fatigue characteristics can be obtained similarly.
As described above, the durability and corrosion resistance of the heat exchanger are dramatically improved by optimizing the components and properties of the core material of the clad material and the surface layer material, and combinations thereof, compared to the case of using conventional materials. It becomes possible to do.
本発明によるクラッド材は、芯材と、芯材の一方の面又は両方の面に表層材が貼り合わされている。以下、芯材、表層材の順に本発明の限定理由を説明する。芯材の一方の面だけに表層材が貼り合わされている場合には、他方の面にはろう材層を貼り合せることができる。なお、以下の「％」は質量％を意味するものとする。 In the clad material according to the present invention, a core material and a surface layer material are bonded to one surface or both surfaces of the core material. Hereinafter, the reasons for limitation of the present invention will be described in the order of the core material and the surface layer material. When the surface layer material is bonded to only one surface of the core material, the brazing material layer can be bonded to the other surface. The following “%” means mass%.
［芯材（化学組成）］
Ｍｎ：０．５〜２．０％
芯材に含まれるＭｎは、基地中にＡｌ-Ｍｎ系金属間化合物として分散し、耐食性を低下させることなく強度を向上させる作用がある。また、Ｓｉと同時に添加することで、微細なＡｌ-Ｍｎ-Ｓｉ系金属間化合物が形成され、強度を向上させる作用を有する。
ただし、０．５％未満では上記による強度向上の効果が不十分であり、一方、２．０％より多いと粗大な化合物が生成するために、鋳造性や圧延などの加工性が低下する。したがって、Ｍｎ含有量は０．５〜２．０％とする。なお、上記と同様の理由で、好ましい範囲は０．７〜１．８％、より好ましい範囲は０．９〜１．６％である。
[Core material (chemical composition)]
Mn: 0.5 to 2.0%
Mn contained in the core material is dispersed as an Al—Mn intermetallic compound in the matrix, and has the effect of improving the strength without reducing the corrosion resistance. Further, by adding simultaneously with Si, a fine Al—Mn—Si intermetallic compound is formed, and has an effect of improving the strength.
However, if it is less than 0.5%, the effect of improving the strength due to the above is insufficient. On the other hand, if it exceeds 2.0%, a coarse compound is produced, so that workability such as castability and rolling deteriorates. Therefore, the Mn content is 0.5 to 2.0%. For the same reason as described above, the preferable range is 0.7 to 1.8%, and the more preferable range is 0.9 to 1.6%.
Ｃｕ：０．１〜１．０％
芯材に含まれるＣｕは、マトリックスに固溶して強度を向上させ、また芯材の電位を貴にし、表層材やその他の犠牲陽極部材との電位差を大きくし、耐食性を向上する作用を有する。
ただし、０．１％未満では強度向上の効果が不十分であり、一方、１．０％より多いと粒界腐食が発生し、耐食性が低下するため好ましくない。したがって、Ｃｕ含有量は０．１〜１．０％とする。なお、上記と同様の理由で、好ましい範囲は０．３〜０．８％、より好ましい範囲は０．４〜０．７％である。
Cu: 0.1 to 1.0%
Cu contained in the core material has the effect of improving the corrosion resistance by improving the strength by solid solution in the matrix, making the potential of the core material noble, increasing the potential difference from the surface layer material and other sacrificial anode members. .
However, if it is less than 0.1%, the effect of improving the strength is insufficient. On the other hand, if it exceeds 1.0%, intergranular corrosion occurs and the corrosion resistance is lowered, which is not preferable. Therefore, the Cu content is 0.1 to 1.0%. For the same reason as described above, the preferable range is 0.3 to 0.8%, and the more preferable range is 0.4 to 0.7%.
Ｓｉ：０．３〜１．０％
芯材に含まれるＳｉは、Ｍｎと共存させることでＡｌ-Ｍｎ-Ｓｉ化合物となって基地中に分散し、あるいは基地中に固溶して強度を向上させる作用を有する。また、Ｍｇと同時に添加することでろう付け後に微細な金属間化合物として析出し、時効硬化により著しく強度を向上させる効果を有する。
ただし、０．３％未満では強度向上の効果が不十分であり、一方、１．０％より多いと芯材の融点を低下させ、粒界腐食が発生するため好ましくない。したがって、Ｓｉ含有量は０．３〜１．０％とする。なお、上記と同様の理由で、好ましい範囲は０．４〜０．９％、より好ましい範囲は０．５〜０．８％である。
Si: 0.3 to 1.0%
Si contained in the core material acts as an Al-Mn-Si compound by coexisting with Mn and is dispersed in the matrix, or has a function of improving the strength by dissolving in the matrix. Moreover, by adding simultaneously with Mg, it precipitates as a fine intermetallic compound after brazing, and has the effect of remarkably improving strength by age hardening.
However, if it is less than 0.3%, the effect of improving the strength is insufficient. On the other hand, if it exceeds 1.0%, the melting point of the core material is lowered and intergranular corrosion occurs, which is not preferable. Therefore, the Si content is set to 0.3 to 1.0%. For the same reason as described above, the preferable range is 0.4 to 0.9%, and the more preferable range is 0.5 to 0.8%.
Ｆｅ：０．１〜１．０％
芯材に含まれるＦｅは、Ａｌ-Ｆｅ、Ａｌ-Ｆｅ-Ｍｎ、Ａｌ-Ｆｅ-Ｍｎ-Ｓｉ系金属間化合物を生成し、強度を向上させる効果を有する。また、ろう付け後の再結晶粒を微細にする効果があり、強度や成形性を向上する作用を有する。
ただし、０．１％未満では上記の効果が不十分であり、一方、１．０％より多いと巨大晶出物が生成し、製造上問題となる。また、芯材の再結晶粒が非常に微細化してろうの流動を阻害するために、ろう付け性が低下する。したがって、Ｆｅ含有量は０．１〜１．０％とする。なお、上記と同様の理由で、好ましい範囲は０．３〜０．７％、より好ましい範囲は０．４〜０．６％である。
Fe: 0.1 to 1.0%
Fe contained in the core material has an effect of generating Al—Fe, Al—Fe—Mn, and Al—Fe—Mn—Si intermetallic compounds and improving the strength. Moreover, there exists an effect which makes the recrystallized grain after brazing fine, and has an effect | action which improves an intensity | strength and a moldability.
However, if the amount is less than 0.1%, the above effect is insufficient. On the other hand, if the amount is more than 1.0%, a giant crystallized product is generated, which causes a problem in production. In addition, the recrystallized grains of the core material become very fine and hinder the flow of the brazing, so that the brazing property is lowered. Therefore, the Fe content is 0.1 to 1.0%. For the same reason as described above, the preferred range is 0.3 to 0.7%, and the more preferred range is 0.4 to 0.6%.
Ｚｎ：０．１〜３．０％
Ｚｎは芯材の電位を卑にするため、クラッド材の電位を低下させ、その添加量を調整することでその他の部材に対する犠牲陽極効果を付与する効果を奏する。
ただし、０．１％未満では上記の効果が不十分であり、一方、３．０％より多いと腐食速度が増大し過ぎるため、好ましくない。したがって、Ｚｎ含有量は、０．１〜３．０％である。なお、上記と同様の理由で、好ましい範囲は０．５〜２．０％、より好ましい範囲は０．７〜１．７％である。
なお、ＺｎはＭｇとともに、芯材の任意添加元素である。
Zn: 0.1-3.0%
Since Zn lowers the potential of the core material, the potential of the clad material is lowered, and by adjusting the addition amount, there is an effect of imparting a sacrificial anode effect to other members.
However, if the amount is less than 0.1%, the above effect is insufficient. On the other hand, if it exceeds 3.0%, the corrosion rate increases excessively, which is not preferable. Therefore, the Zn content is 0.1 to 3.0%. For the same reason as described above, the preferred range is 0.5 to 2.0%, and the more preferred range is 0.7 to 1.7%.
Zn is an optional additive element of the core material together with Mg.
Ｍｇ：０．０１〜１．０％
ＭｇはＳｉと同時に添加されることでろう付け後に微細な金属間化合物として析出し、時効硬化により芯材を著しく強度を向上させる効果を奏する。
ただし、０．０１％未満では上記の効果が不十分であり、一方、１．０％を超えるとろう付け時にフラックスと反応し、ろう付け性が低下する。したがって、Ｍｇ含有量は０．０１〜１．０％である。なお、上記と同様の理由で、好ましい範囲は０．１〜０．８％、より好ましい範囲は０．２〜０．５％である。
芯材は、上記元素を除くと、Ａｌと不可避的不純物からなる。
Mg: 0.01 to 1.0%
When Mg is added simultaneously with Si, it precipitates as a fine intermetallic compound after brazing, and has the effect of significantly improving the strength of the core material by age hardening.
However, if it is less than 0.01%, the above effect is insufficient. On the other hand, if it exceeds 1.0%, it reacts with the flux at the time of brazing, and the brazing property is lowered. Therefore, the Mg content is 0.01 to 1.0%. For the same reason as described above, the preferred range is 0.1 to 0.8%, and the more preferred range is 0.2 to 0.5%.
The core material consists of Al and inevitable impurities, excluding the above elements.
［表層材（耐力）］
本発明の表層材は、以下の理由により、ろう付け後の耐力が３０ＭＰａ以下とされる。
表層材の耐力が低いほど、応力負荷時に塑性変形しやすくなり、本発明のクラッド材に応力緩和作用を付与する。その際、表層材は歪み硬化すると共に、圧縮の応力が残存するため、それに相当するだけの最大負荷応力が低減し、同じ使用環境でも耐久性が著しく向上する。
しかるに、ろう付け後の耐力が３０ＭＰａを超えると、加圧初期に塑性変形が起こり難いため、十分な応力緩和作用が得られにくい。ろう付け後の好ましい耐力は、２５ＭＰａ以下である。
なお、ろう付け後とは、熱交換器にろう付けにより組み付けられた後のことを意味する。ただし、ろう付けと同等の熱処理をクラッド材又は表層材単体に施すことはできるので、本発明におけるろう付け後の耐力とは、この疑似的なろう付け熱処理を行って測定したものを包含する。
[Surface material (proof strength)]
The surface layer material of the present invention has a proof stress after brazing of 30 MPa or less for the following reasons.
The lower the proof stress of the surface layer material, the easier the plastic deformation occurs when stress is applied, and the stress relaxation action is imparted to the clad material of the present invention. At that time, the surface layer material is strain-hardened, and compressive stress remains, so that the corresponding maximum load stress is reduced, and the durability is remarkably improved even in the same use environment.
However, if the proof stress after brazing exceeds 30 MPa, plastic deformation is unlikely to occur in the initial stage of pressurization, and therefore it is difficult to obtain a sufficient stress relaxation action. The preferable yield strength after brazing is 25 MPa or less.
In addition, after brazing means after having been assembled to the heat exchanger by brazing. However, since the heat treatment equivalent to brazing can be performed on the clad material or the surface layer material alone, the proof stress after brazing in the present invention includes those measured by performing this pseudo brazing heat treatment.
［表層材（化学組成）］
Ｚｎ：０．５〜５．０％
表層貼り合せ層中のＺｎは耐力の増加すなわち応力緩和作用を低下させずに、電位を卑にする効果を有する。その結果、表層材が芯材を防食し、貫通孔の発生を抑制するため長期間に渡り耐久性の向上が図れる。また、Ｚｎ添加量を増大しても腐食速度をあまり増大させずに他の部材を犠牲防食することで熱交換器の耐食性を向上させる効果も有する。
ただし、０．５％未満では電位を卑にする効果が十分でなく、耐食性向上効果が不十分となり、一方、５．０％を超えると腐食速度が増大しすぎて、早期に貫通孔が発生する。なお、上記と同様の理由で、好ましい範囲は１．０超〜４．０％、より好ましい範囲は１．５〜３．０％である。
[Surface material (chemical composition)]
Zn: 0.5 to 5.0%
Zn in the surface bonding layer has the effect of lowering the potential without increasing the yield strength, that is, reducing the stress relaxation action. As a result, the surface layer material protects the core material and suppresses the generation of through holes, so that durability can be improved over a long period of time. Moreover, even if it increases Zn addition amount, it has the effect of improving the corrosion resistance of a heat exchanger by sacrificing corrosion prevention of another member, without increasing a corrosion rate so much.
However, if it is less than 0.5%, the effect of lowering the potential is not sufficient, and the effect of improving the corrosion resistance is insufficient. On the other hand, if it exceeds 5.0%, the corrosion rate increases too much and through holes are generated early. To do. For the same reason as described above, the preferred range is more than 1.0 to 4.0%, and the more preferred range is 1.5 to 3.0%.
Ｃｕ,Ｍｇ（各元素がいずれも）：０.０５％未満
これら元素の含有量が増加すると耐力が増大するため、各含有量を０.０５％未満に限定することで、表層材の耐力の増大を抑制し、耐久性向上に必要な応力緩和作用を得る。Ｃｕは電位を貴にする作用を有するため、Ｚｎ含有による効果を阻害する観点からも０.０５％未満に規制する。また、Ｍｇは、ノコロックろう付けにおいてはろう付け性を阻害する観点からも、０.０５％未満に規制するのがよい。もちろん、これら元素は含有量が低いほど好ましいことはいうまでもないが、合計含有量としては０．０８％以下とすることがより好ましい。
Cu, Mg (each element is less than 0.05%) When the content of these elements increases, the yield strength increases. Therefore, by limiting each content to less than 0.05%, the yield strength of the surface layer material can be reduced. It suppresses the increase and obtains the stress relaxation action necessary for improving the durability. Since Cu has a function of making the potential noble, it is restricted to less than 0.05% from the viewpoint of inhibiting the effect of containing Zn. In addition, Mg is preferably regulated to less than 0.05% from the viewpoint of inhibiting brazing in Nocolok brazing. Of course, it is needless to say that the lower the content of these elements, the more the total content is more preferably 0.08% or less.
［表層材（硬さ）］
表層材は、その硬さが小さいほど、応力負荷時に塑性変形しやすく、応力緩和作用が得られやすいので、ろう付け後のビッカース硬さが３５Ｈｖ以下とされる。逆に、当該硬さが３５Ｈｖを超えると表層材の表面が塑性変形し難くなるため、応力緩和作用が得られにくく、十分な耐久性向上効果が得られない。好ましい表層材の表面硬さは３０Ｈｖ以下である。
表層材の硬さ測定はろう付け熱処理時の拡散や測定時に歪み硬化の要素も加わるため、実施の使用環境に近い評価が可能となる。
[Surface material (hardness)]
The smaller the hardness of the surface layer material, the easier it is to plastically deform when stress is applied, and the stress relaxation effect is easily obtained, so the Vickers hardness after brazing is 35 Hv or less. On the other hand, when the hardness exceeds 35 Hv, the surface of the surface layer material is difficult to be plastically deformed, so that it is difficult to obtain a stress relaxation action and a sufficient durability improvement effect cannot be obtained. A preferable surface hardness of the surface layer material is 30 Hv or less.
Since the hardness measurement of the surface layer material includes diffusion during brazing heat treatment and an element of strain hardening during measurement, an evaluation close to the practical use environment is possible.
[ろう材]
Ｓｉ：５．０〜１２.０％
本発明のろう材は、Ａｌ-Ｓｉ系合金からなる。ろう材中に含まれるＳｉは融点を低下させる作用があり、ろう付け熱処理時に溶融ろうを形成し、十分な接合状態を得る効果を有する。
ただし、Ｓｉが５．０％未満では、溶融ろうの生成が少なく、安定した接合状態が得られず、一方、１２．０％より多いと溶融ろうの生成量が増大するため、過剰な溶融ろうの流動によって著しい母材侵食が発生する。したがって、Ｓｉ含有量は５.０〜１２.０％とする。なお、上記と同様の理由で、好ましい範囲は７．０〜１０．０％、より好ましい範囲は８．０〜９．０％である。
[Brazing material]
Si: 5.0 to 12.0%
The brazing material of the present invention is made of an Al-Si alloy. Si contained in the brazing material has the effect of lowering the melting point, and has the effect of forming a molten brazing during the brazing heat treatment and obtaining a sufficient bonding state.
However, if the Si content is less than 5.0%, the production of the molten solder is small, and a stable joining state cannot be obtained. The base metal erosion occurs due to the flow. Therefore, the Si content is 5.0 to 12.0%. For the same reason as described above, the preferable range is 7.0 to 10.0%, and the more preferable range is 8.0 to 9.0%.
以下、本発明を具体的な実施例に基づいて説明する。
［第１実施例］
本発明の熱交換器用アルミニウム合金クラッド材をインナーフィンに適用した例を第１実施例として説明する。
芯材および表層貼り合わせ材として図１に示す組成のアルミニウム合金を半連続鋳造により造塊し、それぞれ所定厚さまで圧延した。なお、図１に示す組成の残部は、Ａｌ及び不可避不純物である（第２実施例も同様）。その後、芯材の両面にクラッド率１０％となるように表層材を熱間圧延してクラッド材を作製した後、厚さ０.３ｍｍと０.１ｍｍまで冷間圧延を行い、３６０℃×３hrのバッチ焼鈍により図１に示すクラッド材（調質Ｏ材）を得た。
板厚０.３ｍｍのクラッド材を波形形状のインナーフィンに、板厚０.１ｍｍのクラッド材をコルゲート成形によりアウターフィンに加工し、電縫溶接にて製造した表裏両面にろう材が設けられたチューブ(芯材組成：Ａｌ-１％Ｍｎ-０.１５％Ｃｕ、ろう材組成：Ａｌ-７.５％Ｓｉ、板厚：０.５ｍｍ)と組み合わせて、ろう付け熱処理を実施して熱交換器を作製した。
ろう付けは各部材が組み付けられた熱交換器をフッ化物系フラックス水溶液中に浸漬して全面に塗布した後、窒素ガス雰囲気中でろう付け温度６００℃に５分間保持した後、１００℃／minで冷却することにより行なった。次の第２実施例も同様である。
Hereinafter, the present invention will be described based on specific examples.
[First embodiment]
The example which applied the aluminum alloy clad material for heat exchangers of this invention to the inner fin is demonstrated as 1st Example.
An aluminum alloy having the composition shown in FIG. 1 was ingoted by semi-continuous casting as a core material and a surface layer bonding material, and each was rolled to a predetermined thickness. The balance of the composition shown in FIG. 1 is Al and inevitable impurities (the same applies to the second embodiment). Thereafter, the surface layer material was hot-rolled so that the clad rate was 10% on both surfaces of the core material to produce a clad material, and then cold-rolled to a thickness of 0.3 mm and 0.1 mm, and 360 ° C. × 3 hr. The clad material (tempered O material) shown in FIG. 1 was obtained by batch annealing.
A clad material with a plate thickness of 0.3 mm was processed into a corrugated inner fin, a clad material with a plate thickness of 0.1 mm was processed into an outer fin by corrugation molding, and brazing material was provided on both front and back surfaces manufactured by electro-welding welding Combined with a tube (core material composition: Al-1% Mn-0.15% Cu, brazing material composition: Al-7.5% Si, plate thickness: 0.5 mm), heat treatment is performed by brazing heat treatment A vessel was made.
Brazing is performed by immersing a heat exchanger in which each member is assembled in a fluoride-based flux aqueous solution, coating the entire surface, holding the brazing temperature at 600 ° C. for 5 minutes in a nitrogen gas atmosphere, and then 100 ° C./min. It was performed by cooling with. The same applies to the second embodiment.
［第２実施例］
次に本発明の熱交換器用アルミニウム合金クラッド材をチューブに適用した例を第２実施例として説明する。
芯材および表層貼り合わせ材として図２に示す組成のアルミニウムを半連続鋳造により造塊し、それぞれ所定厚さまで圧延した。その後、芯材の片面にクラッド率１０％となるように表層材を、他方の面にＡｌ-Ｓｉ系ろう材を熱間圧延してクラッド材を作製した後、厚さ０.５ｍｍまで冷間圧延を行い、３６０℃×３ｈｒのバッチ焼鈍により図２に示すクラッド材（調質Ｏ材）を得た。
得られたクラッド材を電縫溶接にてチューブに加工し、表裏両面にろう材が設けられたインナーフィン(芯材組成：Ａｌ-１％Ｍｎ-０.１５％Ｃｕ、ろう材組成：Ａｌ-７.５％Ｓｉ、板厚：０.３ｍｍ)およびアウターフィン(組成：Ａｌ-１％Ｍｎ-１.５％Ｚｎ、板厚：０.１ｍｍ)と組み合わせて、ろう付け熱処理を実施して熱交換器を作製した。
[Second Embodiment]
Next, the example which applied the aluminum alloy clad material for heat exchangers of this invention to the tube is demonstrated as 2nd Example.
Aluminum having the composition shown in FIG. 2 was ingoted by semi-continuous casting as the core material and the surface layer bonding material, and each was rolled to a predetermined thickness. Thereafter, a surface layer material is formed on one surface of the core material so that the clad rate is 10%, and an Al-Si brazing material is hot-rolled on the other surface to produce a clad material, which is then cooled to a thickness of 0.5 mm. The clad material (tempered O material) shown in FIG. 2 was obtained by batch annealing at 360 ° C. × 3 hr.
The obtained clad material was processed into a tube by electric-welding welding, and inner fins (core material composition: Al-1% Mn-0.15% Cu, brazing material composition: Al-- 7.5% Si, plate thickness: 0.3 mm) and outer fin (composition: Al-1% Mn-1.5% Zn, plate thickness: 0.1 mm) in combination with brazing heat treatment to heat An exchanger was made.
［耐久性評価試験］
第１、第２実施例で作製した熱交換器に室温で周波数１０Ｈｚにて以下の（１）、（２）の条件で高い内圧と低い内圧を各々繰返し負荷する耐久試験を実施し、部材が破断し、内圧が低下するまでの回数を測定した。
（１）０ＭＰａ⇔２．０ＭＰａ
（２）０ＭＰａ⇔０．２ＭＰａ
また、同様に作製した熱交換器について、以下に示す腐食試験を１０００ｈｒ実施し、腐食試験終了後のコアについて、上記と同様に耐久性評価を実施した。
第1実施例の腐食試験（腐食試験１）： ＡＳＴＭ Ｇ８５-Ａ３で規定されているSWAAT(Sea Water Acetic Acid Test)により熱交換器外面側の腐食を促進
第２実施例の腐食試験（腐食試験２）： Ｃｌ−：１００ｐｐｍ、ＳＯ４ ２−：３００ｐｐｍ、Ｆｅ３＋：５０ｐｐｍを含む水溶液(ｐＨ ３.０)を腐食液とし、８０℃に８時間保持した後、室温で１６時間保持するという温度サイクルを加えながら、熱交換器内部を循環させる腐食試験により、熱交換器内面側の腐食を促進
[Durability evaluation test]
The heat exchanger manufactured in the first and second embodiments was subjected to a durability test in which a high internal pressure and a low internal pressure were repeatedly applied at room temperature and a frequency of 10 Hz under the following conditions (1) and (2). The number of times until fracture and the internal pressure decreased were measured.
(1) 0 MPa to 2.0 MPa
(2) 0 MPa to 0.2 MPa
Further, the corrosion test shown below was conducted for 1000 hours on the heat exchanger produced in the same manner, and the durability after the completion of the corrosion test was evaluated in the same manner as described above.
Corrosion test of the first embodiment (corrosion test 1): The SWAAT (Sea Water Acetic Acid Test) specified in ASTM G85-A3 promotes corrosion on the outer surface of the heat exchanger. Corrosion test of the second embodiment (corrosion test) 2): A temperature at which an aqueous solution (pH 3.0) containing Cl − : 100 ppm, SO 4 2− : 300 ppm, Fe 3+ : 50 ppm is used as a corrosive liquid and maintained at 80 ° C. for 8 hours and then at room temperature for 16 hours. Accelerates corrosion on the inner surface of the heat exchanger by a corrosion test that circulates inside the heat exchanger while adding cycles
各耐久試験における測定結果を以下の基準により評価した。
破断までの回数
条件(1) 条件(2)
◎：１００万回以上 ◎：５００万回以上
○： ５０万回以上 ○：２５０万回以上
△： １０万回以上 △：１００万回以上
×： １０万回未満 ×：１００万回未満
評価結果を図１、図２に示す。
The measurement results in each durability test were evaluated according to the following criteria.
Number of times to break
Condition (1) Condition (2)
◎: More than 1 million times ◎: More than 5 million times ○: More than 500,000 times ○: More than 2.5 million times △: More than 100,000 times △: More than 1 million times ×: Less than 100,000 times ×: Less than 1 million times Evaluation result Are shown in FIGS.
［表層材のろう付け熱処理後の耐力］
クラッド材作製時に使用した図１（図２）の組成を有する表層材を単体で０.５ｍｍまで圧延を行い、３６０℃×３hrのバッチ焼鈍により調質Ｏ材のベア材を作製した。その後、窒素ガス雰囲気中で６００℃に５分間保持した後、１００℃／ｍｉｎで冷却するろう付け熱処理を実施し、ＪＩＳ ５号試験片引張試験を実施し、耐力を測定した。その結果を図１、図２に併せて示す。
[Strength after brazing heat treatment of surface layer material]
The surface layer material having the composition shown in FIG. 1 (FIG. 2) used at the time of producing the clad material was rolled alone to 0.5 mm, and a tempered O material bare material was produced by batch annealing at 360 ° C. for 3 hours. Then, after hold | maintaining at 600 degreeC for 5 minute (s) in nitrogen gas atmosphere, the brazing heat processing which cools at 100 degrees C / min was implemented, the JIS No. 5 test piece tensile test was implemented, and the yield strength was measured. The results are also shown in FIGS.
［表層材の硬さ（Ｈｖ）］
図１、図２に示すクラッド材について、窒素ガス雰囲気中で６００℃に５分間保持した後、１００℃／ｍｉｎで冷却するろう付け熱処理を実施し、その後、表面からマイクロビッカース硬さ試験機により、２５ｇｆの加圧力で１５秒保持する条件で圧痕を付与して硬さ測定を行なった。その結果も図１、図２に示す。
[Hardness of surface material (Hv)]
The clad material shown in FIG. 1 and FIG. 2 is held at 600 ° C. for 5 minutes in a nitrogen gas atmosphere, and then subjected to brazing heat treatment at 100 ° C./min, and then from the surface using a micro Vickers hardness tester. Indentation was given under the condition of holding for 15 seconds with a pressure of 25 gf, and the hardness was measured. The results are also shown in FIGS.
本発明のクラッド材を用いて作製されるインナーフィン、チューブの形態に限定はなく、熱交換器を構成する部材に本発明のクラッド材を広く適用することができる。
これ以外にも、本発明の主旨を逸脱しない限り、上記実施の形態で挙げた構成を取捨選択したり、他の構成に適宜変更することが可能である。
The form of the inner fin and the tube manufactured using the clad material of the present invention is not limited, and the clad material of the present invention can be widely applied to members constituting the heat exchanger.
In addition to this, as long as it does not depart from the gist of the present invention, the configuration described in the above embodiment can be selected or changed to another configuration as appropriate.
Claims (4)
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| JP2016133281A Division JP6283069B2 (en) | 2016-07-05 | 2016-07-05 | Heat exchanger |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN106978552A (en) * | 2015-10-26 | 2017-07-25 | 株式会社神户制钢所 | It is surface-treated aluminium alloy and surface treatment aluminum alloy clad sheet |
| CN111270108A (en) * | 2020-03-27 | 2020-06-12 | 江苏鼎胜新能源材料股份有限公司 | Novel alloy high-strength PCB aluminum substrate aluminum material and preparation method thereof |
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| US20040185293A1 (en) * | 2001-05-03 | 2004-09-23 | Morten Syslak | Brazing sheet |
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| CN106978552A (en) * | 2015-10-26 | 2017-07-25 | 株式会社神户制钢所 | It is surface-treated aluminium alloy and surface treatment aluminum alloy clad sheet |
| CN111270108A (en) * | 2020-03-27 | 2020-06-12 | 江苏鼎胜新能源材料股份有限公司 | Novel alloy high-strength PCB aluminum substrate aluminum material and preparation method thereof |
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| JP6262930B2 (en) | 2018-01-17 |
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