JP2690054B2 - High strength Al alloy for pipe fittings of Al heat exchanger - Google Patents
High strength Al alloy for pipe fittings of Al heat exchangerInfo
- Publication number
- JP2690054B2 JP2690054B2 JP63109721A JP10972188A JP2690054B2 JP 2690054 B2 JP2690054 B2 JP 2690054B2 JP 63109721 A JP63109721 A JP 63109721A JP 10972188 A JP10972188 A JP 10972188A JP 2690054 B2 JP2690054 B2 JP 2690054B2
- Authority
- JP
- Japan
- Prior art keywords
- brazing
- alloy
- strength
- less
- heat exchanger
- 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.)
- Expired - Fee Related
Links
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- Details Of Heat-Exchange And Heat-Transfer (AREA)
- Laminated Bodies (AREA)
Description
【発明の詳細な説明】 〔産業上の利用分野〕 この発明は、Al熱交換器の構造部材である管継手とし
て用いるのに適し、かつAl熱交換器を真空ろう付けある
いはフラックスろう付けにより組立て製造する際に、管
継手の管材への取付けを、この他の構造部材であるフィ
ン材やヘッダープレート材などのろう付けと一緒に行な
うことを可能とする高強度Al合金に関するものである。The present invention is suitable for use as a pipe joint, which is a structural member of an Al heat exchanger, and the Al heat exchanger is assembled by vacuum brazing or flux brazing. The present invention relates to a high-strength Al alloy capable of mounting a pipe joint to a pipe material together with brazing of other structural members such as a fin material and a header plate material during manufacturing.
一般に、Al熱交換器は、例えばいずれも純Alあるいは
Al合金で構成された管材、フィン材、およびヘッダープ
レート材などを所定形状に組立て、これを真空ろう付け
あるいはフラックスろう付けによりろう付け結合し、さ
らにこのろう付け前か後に、ろう付け組立て体の構造部
材である管材に、押出し形材を切断し、この切断材にネ
ジ加工などを施すことにより成形された管継手を、純Al
やAl合金を溶加材として用い、隅肉溶接する２工程にて
製造されている。Generally, Al heat exchangers are, for example, pure Al or
Assemble pipe material, fin material, header plate material, etc. made of Al alloy into a predetermined shape, and braze them together by vacuum brazing or flux brazing, and further before or after this brazing, A pipe joint formed by cutting an extruded shape material into a pipe material that is a structural member and performing screw processing on the cut material is pure Al.
It is manufactured in two steps of fillet welding using Al alloy as a filler metal.
上記のAl熱交換器の製造において、ろう付け工程とは
別に管継手を溶接するのは、管継手には強度が要求さ
れ、したがってその製造には、重量％で（以下％は重量
％を示す）、 Zn:4〜５％、Mg:1〜２％、 Mn:0.2〜0.7％、 を含有し、残りがAl不可避不純物からなる組成を有する
JIS7N01などのAl合金が広く用いらており、このAl合金
が、通常600〜620℃、場合によっては640℃という高温
のろう付け温度起に加熱されると、真空ろう付けでは、
合金成分であるZnやMgが蒸発し、特に表面部におけるこ
れらの成分の含有量低下は著しく、これに伴って強度が
低下するようになるばかりでなく、この種Al合金は酸化
皮膜が厚いので、ろう付け性が悪く、またフラックスろ
う付けでは、フラックスと合金成分であるMgとが反応
し、接合を阻害するという理由によるものである。In the production of the above Al heat exchanger, welding the pipe joint separately from the brazing process requires strength in the pipe joint, and therefore the production of the pipe joint is performed by weight% (hereinafter,% means weight%). ), Zn: 4 to 5%, Mg: 1 to 2%, Mn: 0.2 to 0.7%, with the balance being Al inevitable impurities.
Al alloys such as JIS7N01 are widely used, and when this Al alloy is heated to a high brazing temperature of usually 600 to 620 ° C, and in some cases 640 ° C, in vacuum brazing,
Zn and Mg which are alloy components evaporate, and the content of these components is remarkably reduced particularly in the surface portion, and not only the strength is reduced accordingly, but also because this type of Al alloy has a thick oxide film. The reason is that the brazing property is poor, and in the flux brazing, the flux reacts with Mg which is an alloy component to hinder the joining.
このように従来Al熱交換器の製造には、ろう付け組立
てとは別に、管継手の溶接を行なう２工程をとらざるを
得ないために、生産性の点で問答があり、コスト高とな
らざるを得ないのが現状である。As described above, in the conventional manufacturing of the Al heat exchanger, in addition to the brazing and assembling, there is no choice but to perform the two steps of welding the pipe joint, and therefore there is a question and answer in terms of productivity, and the cost is not high. The current situation is unavoidable.
そこで、本発明者等は、上述のような観点から、管継
手の管材への接合を、管材へのフィン材およびヘッダー
プレート材の組立てろう付け時に一緒に行なうことがで
きる管継手用Al合金を開発すべく研究を行なった結果、 上記の従来管継手用高強度Al合金におけるZnおよびMg
成分の含有量を低減して、Zn:0.5〜３％未満およびMg:
0.05〜１％未満とすると、真空ろう付けでは、ZnやMg成
分の蒸発、並びに合金自体の酸化皮膜の形成が極力抑制
されるようになるばかりでなく、フラックスろう付けで
も、Mg成分がフラックスと反応することが著しく抑制さ
れるようになるので、良好なろう付けが可能となって、
強固なろう付け強度が確保できることから、ろう付け工
程だけの一工程でAl熱交換器の製造が可能となり、一方
合金自体のZnおよびMg含有量の低減による強度低下は、
0.3〜1.3％のSi成分の含有によって、これを向上させる
ことができ、さらに0.31〜0.8％のCuの含有は一段の強
度向上、そして0.01〜0.1％Ti、0.01〜0.15％のZrの含
有は押出加工性の一段の向上をもたらすという知見を得
たのである。Therefore, the inventors of the present invention, from the above-described viewpoint, provide an Al alloy for a pipe joint, which can join the pipe joint to the pipe material together when assembling and brazing the fin material and the header plate material to the pipe material. As a result of research for development, Zn and Mg in the above high-strength Al alloy for conventional pipe joints
By reducing the content of the components, Zn: 0.5 to less than 3% and Mg:
If it is less than 0.05 to 1%, not only evaporation of Zn and Mg components and formation of oxide film of the alloy itself are suppressed as much as possible by vacuum brazing, but also by flux brazing, Mg components become flux. Since the reaction will be significantly suppressed, good brazing is possible,
Since it is possible to secure a strong brazing strength, it becomes possible to manufacture an Al heat exchanger in a single step only in the brazing step, while the strength decrease due to the reduction of Zn and Mg contents of the alloy itself is
This can be improved by the inclusion of 0.3-1.3% Si component, and the inclusion of 0.31-0.8% Cu further improves the strength, and the inclusion of 0.01-0.1% Ti, 0.01-0.15% Zr We have obtained the finding that it can further improve extrusion processability.
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、 Zn:0.5〜３％未満、Mg:0.05〜１％未満、 Mn:0.1〜1.2％、Si:0.3〜1.3％、 を含有し、さらに、 Ti:0.01〜0.1％、Zr:0.01〜0.15％、 Cu:0.31〜0.8％、 のうちの１種または２種以上を含有し、残りがAlと不可
避不純物からなる組成を有するAl熱交換器の管継手用高
強度Al合金に特徴を有するものである。The present invention was made based on the above findings, and contains Zn: 0.5 to less than 3%, Mg: 0.05 to less than 1%, Mn: 0.1 to 1.2%, Si: 0.3 to 1.3%, Furthermore, Al heat exchange containing Ti: 0.01 to 0.1%, Zr: 0.01 to 0.15%, Cu: 0.31 to 0.8%, and one or more of them, with the balance being Al and inevitable impurities. It is characterized by a high-strength Al alloy for pipe joints in vessels.
つぎに、この発明のAl合金において、成分組成を上記
の通りに限定した理由を説明する。Next, the reason why the composition of the Al alloy of the present invention is limited as described above will be explained.
（ａ） ZnおよびMg これらの成分には、共存した状態で、ろう付け後に室
温保持の時効硬化で合金強度を向上させる作用がある
が、その含有量が、Zn:0.5％未満およびMg:0.05％未満
では所望の強度を確保することができず、一方その含有
量がZn:3％以上、Mg:1％以上になると、上記の通りろう
付け時における成分蒸発、酸化皮膜の形成、およびフラ
ックスとの反応を抑制することがきわめて困難となり、
良好なろう付けが不可能となり、ろう付け工程だけの一
工程でAl熱交換器を製造することができなくなることか
ら、それぞれのその含有量を、Zn:0.5〜３％未満、Mg:
0.05〜１％未満と定めた。(A) Zn and Mg In the coexistence state, these components have the effect of improving the alloy strength by age hardening at room temperature after brazing, but their contents are Zn: less than 0.5% and Mg: 0.05. If the content is less than%, the desired strength cannot be secured. On the other hand, if the content is Zn: 3% or more and Mg: 1% or more, as described above, component evaporation during brazing, formation of oxide film, and flux It becomes extremely difficult to suppress the reaction with
Since good brazing becomes impossible and it becomes impossible to produce an Al heat exchanger by only one step of brazing, the content of each of them is Zn: 0.5 to less than 3%, Mg:
It was defined as 0.05 to less than 1%.
（ｂ） MnおよびSi これらの成分には、Alと結合してAl−Mn−Si系化合物
を形成し、この化合物は、特にろう付け時に、ろう付け
加熱温度である600℃程度の温度で素地中に微細均一に
分散析出して強度を向上させる作用があるが、その含有
量がMn:0.1％未満およびSi:0.3％未満では、上記化合物
の形成が不十分で所望の高強度を確保することができ
ず、一方その含有量がMn:1.2％およびSi:1.3％をそれぞ
れ越えてもより一層の強度向上効果が現われないばかり
でなく、Mnについては押出加工性が低下し、またSiにつ
いてはろう付け時に溶融し易くなることから、その含有
量をそれぞれMn:0.1〜1.2％、Si:0.3〜1.3％と定めた。(B) Mn and Si These components combine with Al to form an Al-Mn-Si-based compound, and this compound forms a base material at a brazing heating temperature of about 600 ° C, especially during brazing. Although it has the effect of improving the strength by finely and uniformly dispersing and precipitating in it, if its content is less than Mn: 0.1% and Si: less than 0.3%, the formation of the above compound is insufficient to secure the desired high strength. On the other hand, even if the content exceeds Mn: 1.2% and Si: 1.3% respectively, the effect of further improving the strength does not appear, and the extrusion processability of Mn decreases and Since it becomes easy to melt during brazing, its contents were set to Mn: 0.1 to 1.2% and Si: 0.3 to 1.3%, respectively.
（ｃ） Cu Cu成分には、素地に固溶して、これを固溶強化し、上
記の微細なAl−Mn−Si系化合物との相乗効果によって、
強度を一段と向上させる作用があるので含有されるが、
その含有量が0.31％未満では所望の強度向上効果が得ら
れず、一方その含有量が0.8％を越えると、押出加工性
が低下すると共に、耐食性も劣化するようになることか
ら、その含有量を0.31〜0.8％と定めた。(C) Cu The Cu component is solid-solved in the matrix to strengthen it, and by the synergistic effect with the fine Al-Mn-Si-based compound,
It is contained because it has the effect of further improving strength,
If the content is less than 0.31%, the desired strength-improving effect cannot be obtained, while if the content exceeds 0.8%, the extrusion processability decreases and the corrosion resistance also deteriorates. Was set to 0.31 to 0.8%.
（ｄ） TiおよびZr 上記のように管継手は、例えば断面が６角形の長尺材
を押出加工により成形し、これを所定長さに切断し、こ
の切断片に穴あけ加工やネジ切り加工、さらにグライン
ダー加工などを施すことにより製造されるために、すぐ
れた押出加工性を具備することが要求され、この発明の
Al合金はすぐれた押出加工性を有すが、さらに一段の押
出加工性が要求される場合にTiおよびZrが含有されるも
のであり、したがって、その含有量がTiおよびZrとも0.
01％未満では所望の押出加工性向上効果が得られず、一
方その含有量がTi:0.1％、Zr:0.15％を越えると押出加
工性が急激に低下するようになることから、その含有量
をそれぞれTi:0.01〜0.1％、Zr:0.01〜0.15％と定め
た。(D) Ti and Zr As described above, the pipe joint is formed, for example, by extruding a long material having a hexagonal cross section, cutting it into a predetermined length, and punching or threading the cut piece. Further, since it is manufactured by subjecting it to grinder processing, it is required to have excellent extrusion processability.
Although the Al alloy has excellent extrudability, Ti and Zr are contained when a further step of extrudability is required, so that the content of both Ti and Zr is 0.
If it is less than 01%, the desired effect of improving the extrudability cannot be obtained. On the other hand, if the content exceeds Ti: 0.1% and Zr: 0.15%, the extrudability will drop sharply. Were determined to be Ti: 0.01 to 0.1% and Zr: 0.01 to 0.15%, respectively.
つぎに、この発明のAl合金を実施例により具体的に説
明する。Next, the Al alloy of the present invention will be specifically described by way of Examples.
通常の溶解法により、それぞれ第１表に示される成分
組成をもったAl合金溶湯を調製し、鋳造して直径:200mm
のビレットとし、このビレットを温度:530℃に８時間保
持の条件で均質化処理した後、500℃の温度で熱間押出
加工して、断面が一辺長さ:15mmの６角形形状を有する
管継手素材としての本発明Al合金材１〜10および従来Al
合金材１〜３をそれぞれ製造した。An Al alloy melt having the composition shown in Table 1 was prepared by the usual melting method, cast, and the diameter was 200 mm.
This billet is homogenized at a temperature of 530 ° C for 8 hours and then hot extruded at a temperature of 500 ° C to form a hexagonal tube with a side length of 15 mm. Inventive Al alloy materials 1 to 10 and conventional Al as joint materials
Alloy materials 1 to 3 were manufactured.
ついで、これらのAl合金材より、断面:15mm×2mm、長
さ:100mmの引張試験片、および幅:15mm×長さ:30mm×厚
さ:1.5mmのろう付試験片を切出し、まず強度を評価する
目的で、前記引張試験片を用い、これに真空ろう付けに
相当する条件、すなわち10-4torrの真空中、温度:600℃
の５分間保持の条件で加熱処理を加え、この加熱後、30
日間室温保持（時効硬化）した時点で、引張強さを測定
すると共に、前記ろう付試験片を、Mn:1.23％、Cu:0.12
％を含有し、残りがAlと不可避不純物からなる組成を有
し、かつ幅:10mm×長さ:30mm×厚さ:1mmの寸法をもった
板材の上面に逆Ｔ字形に立設配置し、溶加材として直
径:1.6mmを有する下記組成のAl合金線材を用い、これを
両側ろう付けコーナー部にセットし、 （ａ） Al−10.5％Siの組成を有する上記溶加材にフラ
ックスを散布し、N2ガス雰囲気中で、600℃に５分間保
持（以下ろう付け条件ａという）、 （ｂ） Al−10.0％Si−1.2％Mgの組成を有する上記溶
加材を用い、10-4torrの真空中で、600℃に５分間保持
（以下ろう付け条件ｂという）、 以上（ａ）または（ｂ）のいずれかの条件でろう付けを
行ない、ろう付け後、上記板材を上から押さえて固定し
た状態で上記ろう付試験片を垂直に引張ることにより ろう付け強度を測定した。これらの結果を第１表に示し
た。Then, from these Al alloy materials, a cross-section: 15 mm × 2 mm, a length: 100 mm tensile test piece, and a width: 15 mm × length: 30 mm × thickness: 1.5 mm brazing test piece are cut out, and the strength is first cut. For the purpose of evaluation, the tensile test piece was used, and the conditions equivalent to vacuum brazing, that is, in a vacuum of 10 −4 torr, temperature: 600 ° C.
Heat treatment under the condition of holding for 5 minutes, and after this heating,
Tensile strength was measured at the time of room temperature retention (age hardening) for one day, and the brazing test piece was measured with Mn: 1.23%, Cu: 0.12
%, The rest of which has a composition consisting of Al and unavoidable impurities, and is vertically arranged in an inverted T shape on the upper surface of a plate material having dimensions of width: 10 mm x length: 30 mm x thickness: 1 mm. An Al alloy wire having the following composition having a diameter of 1.6 mm is used as a filler material, and it is set at both sides of the brazing corners, and (a) a flux is sprinkled on the filler material having a composition of Al-10.5% Si. And kept at 600 ° C. for 5 minutes in an N 2 gas atmosphere (hereinafter referred to as brazing condition a), (b) using the above-mentioned filler material having a composition of Al-10.0% Si-1.2% Mg, 10 -4 Hold at 600 ° C for 5 minutes in a torr vacuum (hereinafter referred to as brazing condition b), perform brazing under either condition (a) or (b) above, and then press the above plate material from above after brazing. By vertically pulling the brazing test piece with The brazing strength was measured. The results are shown in Table 1.
第１表に示される結果から、本発明Al合金材１〜10
は、いずれもろう付け加熱後（時効硬化も含む）におい
ても高強度を有し、かつ真空ろう付けおよびフラックス
ろう付けのいずれでも著しく高いろう付け強度を示し、
ろう付けが良好に行なわれていることを示すのに対し
て、従来Al合金材１〜３は、ろう付け加熱時のMgやZn成
分の蒸発が著しいため強度低下があり、さらにこれに加
えて強固な酸化皮膜の形成およびフラックスとの反応が
原因で、真空ろう付けおよびフラックスろう付けとも不
可能であることが明らかである。From the results shown in Table 1, the present invention Al alloy materials 1-10
Has high strength even after heating for brazing (including age hardening), and shows extremely high brazing strength in both vacuum brazing and flux brazing,
In contrast to the fact that the brazing is performed well, the conventional Al alloy materials 1 to 3 have a decrease in strength due to significant evaporation of Mg and Zn components during brazing heating. It is apparent that neither vacuum brazing nor flux brazing is possible due to the formation of a strong oxide film and the reaction with the flux.
上述のように、この発明のAl合金は、真空ろう付けで
は、合金成分の蒸発、並びに酸化皮膜の形成が著しく少
なく、さらにフラックスろう付けでは合金成分とフラッ
クスとの反応がないので、良好なろう付けが可能とな
り、高いろう付け強度が確保されることから、Al熱交換
器の管継手として用いた場合に、他の構造部材であるフ
ィン材や管材、さらにヘッダープレート材などのろう付
け組立てと同時に、管材へのろう付けが可能となり、こ
の結果一工程のろう付けでAl熱交換器を製造することが
できるようになり、また前記のように合金成分の蒸発が
抑制されるので、合金特性の局部的不均一性が解消され
て、ろう付け後も高い強度を保持するなど工業上有用な
特性を有するのである。As described above, the Al alloy of the present invention is excellent in vaporization of the alloy components and the formation of an oxide film in the vacuum brazing, and further, in the flux brazing, there is no reaction between the alloy components and the flux. Since it can be brazed and high brazing strength is secured, when used as a pipe joint of an Al heat exchanger, it can be used for brazing and assembling other structural members such as fin materials and pipe materials, and header plate materials. At the same time, it becomes possible to braze the pipe material, and as a result, it becomes possible to manufacture the Al heat exchanger by one-step brazing, and as described above, the evaporation of alloy components is suppressed, so that the alloy characteristics It has industrially useful properties such as elimination of local non-uniformity and retention of high strength even after brazing.
───────────────────────────────────────────────────── フロントページの続き (56)参考文献 特開 昭62−177142（ＪＰ，Ａ) 特開 昭61−99654（ＪＰ，Ａ) ─────────────────────────────────────────────────── ─── Continuation of the front page (56) References JP-A-62-177142 (JP, A) JP-A-61-99654 (JP, A)
Claims (3)
重量％）を有することを特徴とするAl熱交換器の管継手
用高強度Al合金。1. Zn: 0.5 to less than 3%, Mg: 0.05 to less than 1%, Mn: 0.1 to 1.2%, Si: 0.3 to 1.3%, and Cu: 0.31 to 0.8%. A high-strength Al alloy for a pipe joint of an Al heat exchanger, characterized in that the balance thereof is a composition of Al and unavoidable impurities (above wt%).
避不純物からなる組成（以上重量％）を有することを特
徴とするAl熱交換器の管継手用高強度Al合金。2. Zn: 0.5 to less than 3%, Mg: 0.05 to less than 1%, Mn: 0.1 to 1.2%, Si: 0.3 to 1.3%, and Ti: 0.01 to 0.1%, Zr: High strength Al for pipe joints of Al heat exchangers, characterized by containing one or more of 0.01 to 0.15%, and the balance of Al and unavoidable impurities (above wt%) alloy.
重量％）を有することを特徴とするAl熱交換器の管継手
高強度Al合金。3. Zn: 0.5 to less than 3%, Mg: 0.05 to less than 1%, Mn: 0.1 to 1.2%, Si: 0.3 to 1.3%, and Ti: 0.01 to 0.1%, Zr: 0.01 to 0.15%, 1 or 2 or more of them, and Cu: 0.31 to 0.8%, with the balance being Al and unavoidable impurities. Exchanger pipe fittings High strength Al alloy.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63109721A JP2690054B2 (en) | 1988-05-02 | 1988-05-02 | High strength Al alloy for pipe fittings of Al heat exchanger |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63109721A JP2690054B2 (en) | 1988-05-02 | 1988-05-02 | High strength Al alloy for pipe fittings of Al heat exchanger |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH01279728A JPH01279728A (en) | 1989-11-10 |
| JP2690054B2 true JP2690054B2 (en) | 1997-12-10 |
Family
ID=14517541
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP63109721A Expired - Fee Related JP2690054B2 (en) | 1988-05-02 | 1988-05-02 | High strength Al alloy for pipe fittings of Al heat exchanger |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2690054B2 (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH089750B2 (en) * | 1991-01-14 | 1996-01-31 | 株式会社神戸製鋼所 | High strength aluminum alloy with excellent brazeability |
| JP7222047B1 (en) * | 2021-09-28 | 2023-02-14 | 株式会社Uacj | Aluminum alloy extruded material for piping connector, manufacturing method thereof, and piping connector |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6199654A (en) * | 1984-10-22 | 1986-05-17 | Furukawa Alum Co Ltd | Al alloy for connector |
| JPH0653905B2 (en) * | 1986-01-30 | 1994-07-20 | 三菱アルミニウム株式会社 | Al alloy for heat exchanger fin material |
-
1988
- 1988-05-02 JP JP63109721A patent/JP2690054B2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| JPH01279728A (en) | 1989-11-10 |
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