JPH038569A - Production of heat exchanger made of aluminum - Google Patents
Production of heat exchanger made of aluminumInfo
- Publication number
- JPH038569A JPH038569A JP13037889A JP13037889A JPH038569A JP H038569 A JPH038569 A JP H038569A JP 13037889 A JP13037889 A JP 13037889A JP 13037889 A JP13037889 A JP 13037889A JP H038569 A JPH038569 A JP H038569A
- Authority
- JP
- Japan
- Prior art keywords
- brazing
- alloy
- heat exchanger
- core material
- strength
- 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.)
- Pending
Links
- 229910052782 aluminium Inorganic materials 0.000 title claims description 7
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 title claims description 7
- 238000004519 manufacturing process Methods 0.000 title claims description 7
- 238000005219 brazing Methods 0.000 claims abstract description 68
- 239000000956 alloy Substances 0.000 claims abstract description 34
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 34
- 239000011162 core material Substances 0.000 claims abstract description 23
- 238000001816 cooling Methods 0.000 claims abstract description 18
- 229910000838 Al alloy Inorganic materials 0.000 claims abstract description 12
- 239000000945 filler Substances 0.000 claims abstract description 10
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 239000000463 material Substances 0.000 claims description 23
- 238000010438 heat treatment Methods 0.000 claims description 21
- 238000000034 method Methods 0.000 claims description 8
- 229910052751 metal Inorganic materials 0.000 abstract description 8
- 239000002184 metal Substances 0.000 abstract description 8
- 238000005253 cladding Methods 0.000 abstract description 5
- 229910052719 titanium Inorganic materials 0.000 abstract description 3
- 229910052796 boron Inorganic materials 0.000 abstract description 2
- 229910052804 chromium Inorganic materials 0.000 abstract description 2
- 229910052735 hafnium Inorganic materials 0.000 abstract description 2
- 229910052742 iron Inorganic materials 0.000 abstract description 2
- 229910052748 manganese Inorganic materials 0.000 abstract description 2
- 229910052726 zirconium Inorganic materials 0.000 abstract description 2
- 229910052802 copper Inorganic materials 0.000 abstract 1
- 230000000694 effects Effects 0.000 description 11
- 238000005260 corrosion Methods 0.000 description 8
- 230000007797 corrosion Effects 0.000 description 8
- 239000000203 mixture Substances 0.000 description 8
- 238000005266 casting Methods 0.000 description 4
- 239000002244 precipitate Substances 0.000 description 4
- 150000001875 compounds Chemical class 0.000 description 2
- 229910000765 intermetallic Inorganic materials 0.000 description 2
- 239000007788 liquid Substances 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 239000003507 refrigerant Substances 0.000 description 2
- 239000011347 resin Substances 0.000 description 2
- 229920005989 resin Polymers 0.000 description 2
- 229910001220 stainless steel Inorganic materials 0.000 description 2
- 229910018182 Al—Cu Inorganic materials 0.000 description 1
- 229910001020 Au alloy Inorganic materials 0.000 description 1
- 229910017818 Cu—Mg Inorganic materials 0.000 description 1
- 101000874049 Magnolia grandiflora Beta-cubebene synthase Proteins 0.000 description 1
- 229910019752 Mg2Si Inorganic materials 0.000 description 1
- ZLMJMSJWJFRBEC-UHFFFAOYSA-N Potassium Chemical compound [K] ZLMJMSJWJFRBEC-UHFFFAOYSA-N 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 238000004210 cathodic protection Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000012733 comparative method Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000001035 drying Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000004907 flux Effects 0.000 description 1
- 239000003353 gold alloy Substances 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 229910052700 potassium Inorganic materials 0.000 description 1
- 239000011591 potassium Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 230000002040 relaxant effect Effects 0.000 description 1
- 150000003839 salts Chemical class 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000000725 suspension Substances 0.000 description 1
- 238000010998 test method Methods 0.000 description 1
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明は、アルミニウム製熱交換器の製造方法に関する
もので、特にろう付け後の常温強度を改善したものであ
る。DETAILED DESCRIPTION OF THE INVENTION [Industrial Field of Application] The present invention relates to a method for manufacturing an aluminum heat exchanger, and in particular improves the room temperature strength after brazing.
一般にアルミニウム製熱交換器、特に自動車用熱交換器
であるラジェータ、ヒータ、オイルクーラー及びエアコ
ン用エバポレータやコンデンサー等の多くはろう付け工
法により組立てられている。In general, many aluminum heat exchangers, especially automobile heat exchangers such as radiators, heaters, oil coolers, and air conditioner evaporators and condensers, are assembled by the brazing method.
これ等の熱交換器は、第2図に示すようにプレート成形
体f4)、 f4’)を組合せて冷媒通路(5)を形成
し、該通路(5)間にフィン(6)を取付けたドロンカ
ップタイプのエバポレーターやオイルクーラーでは、3
003系合金を芯材とし、その表面にAl合金ろう材を
クラッドしたブレージングシートが用いられている。ま
た第3図に示すようにチューブ(7)間にフィン(6)
を取付け、チューブ(7)の両端に座板(8)を設け、
該座板(8)にバッキング(9)を介して樹脂製タンク
(10)を取付けたラジェータでは、座板とチューブに
3003系合金を芯材とし、その内側となる片面に10
70合金や7072合金などの犠牲陽極層をクラッドし
、その反対面にAl合金ろう材をクラッドしたブレージ
ングシートが用いられている。These heat exchangers, as shown in Figure 2, combine plate moldings f4) and f4') to form a refrigerant passage (5), and fins (6) are installed between the passages (5). For Dron cup type evaporators and oil coolers, 3
A brazing sheet is used in which the core material is a 003 series alloy and the surface thereof is clad with an Al alloy brazing material. Also, as shown in Figure 3, there are fins (6) between the tubes (7).
, install seat plates (8) on both ends of the tube (7),
In a radiator in which a resin tank (10) is attached to the seat plate (8) via a backing (9), the seat plate and tube are made of 3003 series alloy as a core material, and one side of the inner side is made of 3003 series alloy.
A brazing sheet is used in which a sacrificial anode layer such as 70 alloy or 7072 alloy is clad, and the opposite side is clad with an Al alloy brazing material.
近年熱交換器の軽量化、コスト低減のため熱交換器部材
の薄肉化が要求されるようになった。In recent years, there has been a demand for thinner heat exchanger members in order to reduce the weight and cost of heat exchangers.
しかしながら従来用いられている3003合金等を芯材
とするブレージングシートでは、ろう付け加熱後の強度
が低く、薄肉化が困難となっている。このため熱交換器
としての強度を維持するため、種々の高強度合金の開発
が試みられ、熱処理合金等の高強度合金が提案されてい
るが、何れも現行のろう付け条件による強度向上には限
界がある。また耐食性の面がら冷却速度が遅い場合には
、粒界に添加元素が析出し、粒界腐食の発生が増長され
る問題がある。However, conventionally used brazing sheets having a core material such as 3003 alloy have low strength after brazing and heating, making it difficult to reduce the thickness. Therefore, in order to maintain the strength of the heat exchanger, attempts have been made to develop various high-strength alloys, and high-strength alloys such as heat-treated alloys have been proposed, but none of them can improve the strength under the current brazing conditions. There is a limit. In addition, if the cooling rate is slow from the viewpoint of corrosion resistance, there is a problem in that additive elements precipitate at grain boundaries, increasing the occurrence of intergranular corrosion.
本発明はこれに鑑み種々検討の結果、ろう付け後の冷却
速度を高くすることにより、強度が向上することを知見
し、更に検討の結果、高強度、薄肉熱交換器の製造を可
能にする高強度アルミニウム製熱交換器の製造方法を開
発したものである。In view of this, as a result of various studies, the present invention has found that the strength can be improved by increasing the cooling rate after brazing.As a result of further studies, the present invention has made it possible to manufacture a high-strength, thin-walled heat exchanger. A method for manufacturing high-strength aluminum heat exchangers has been developed.
即ち本発明の一つは、Si0.4〜1,211%(以下
wt%を%と略記) 、 F e 0.15〜1.0
%Cu0.4〜1.0%、 Mn0.5〜1.2%、M
g0.05〜0.8%を含み、更にCr 0.00[〜
0.5%。That is, one of the aspects of the present invention is Si 0.4 to 1,211% (hereinafter wt% is abbreviated as %), Fe 0.15 to 1.0
%Cu0.4-1.0%, Mn0.5-1.2%, M
g0.05-0.8%, and further contains Cr 0.00[~
0.5%.
Z r 0.001〜0.3%、 Hf0.001〜
1.5%。Zr 0.001~0.3%, Hf0.001~
1.5%.
T i 0.001〜0.5%、 Bo、0001〜
01%の範囲内で何れか1種又は2種以上を含み、残部
)\aと不可避的不純物からなる合金を芯材とし、その
片面又は両面にSi5%以上を含むA/金合金う材をク
ラットしたブレージングシートを、熱交換器部材に使用
して熱交換器を組合せ、ろう付け温度に加熱保持後、5
00℃から200 ℃まで150℃/min以上の速度
で冷却することを特徴とするものである。T i 0.001~0.5%, Bo, 0001~
A/gold alloy material containing 5% or more of Si on one or both sides of which the core material is an alloy consisting of one or two or more of the above within the range of 0.01% and the remainder is \a and unavoidable impurities. The cratted brazing sheet is used as a heat exchanger member to assemble the heat exchanger, and after heating and maintaining it at the brazing temperature,
It is characterized by cooling from 00°C to 200°C at a rate of 150°C/min or more.
また本発明の他の一つは、Si0.4〜12%F e
0.15〜1.0%、 Cu0.4〜1.0%、Mn
0.5〜1.2%、Mg0.05〜08%を含み、更に
Cr 0.001〜0.5%、 Z r0.001〜
0.3%。Another aspect of the present invention is Si0.4 to 12% Fe
0.15-1.0%, Cu0.4-1.0%, Mn
0.5-1.2%, Mg 0.05-08%, further Cr 0.001-0.5%, Z r0.001-
0.3%.
Hf 0.001〜15%、Ti0.001〜0.5%
、B0.000+−0,1%の範囲内で何れか1種又は
2種以上を含み、残部Alと不可避的不純物からなる合
金を芯材とし、その片面にSi5%以上を含むAl合金
ろう材をクラッドし、反対面に芯材より50m V以上
卑な電位を有するAl合金皮材をクラッドしたブレージ
ングシートを、熱交換器部材に使用して熱交換器を組合
せ、ろう付け温度に加熱保持後、500℃から200℃
まで1508C/min以上の速度で冷却することを特
徴とするものである。Hf 0.001-15%, Ti 0.001-0.5%
, B0.000+-0.1%, and the balance is Al and unavoidable impurities, and the core material is an alloy containing 5% or more of Si on one side. A brazing sheet clad with Al alloy skin material having a potential 50 mV or more more base than the core material on the opposite side is used as a heat exchanger member, and the heat exchanger is assembled, and after heating and holding at the brazing temperature. , 500℃ to 200℃
It is characterized by cooling at a rate of 1508 C/min or more.
本発明において芯材組成を上記の如く限定したのは、次
の理由によるものである。The reason why the core material composition is limited as described above in the present invention is as follows.
Siはろう付け加熱によりマトリックス中に固溶し、強
度を向上させ、更にろう付け加熱後の冷却時及び冷却後
に室温に放置されたときに、Mgと共に微細なMg25
iを析出して材料強度を向上させる。しかしてS1含有
量を0.4〜1.2%と限定したのは、0.4%未満で
はろう付け後の強度が十分でなく、1.2%を越えると
固相線温度が低くなり、ろう付け加熱時に溶融する恐れ
が生ずるためである。Si forms a solid solution in the matrix during brazing heating, improves strength, and also forms fine Mg25 with Mg during cooling after brazing heating and when left at room temperature after cooling.
i is precipitated to improve material strength. However, the S1 content was limited to 0.4 to 1.2% because if it is less than 0.4%, the strength after brazing will not be sufficient, and if it exceeds 1.2%, the solidus temperature will be low. This is because there is a risk of melting during brazing heating.
Feは芯材の結晶粒を微細化し、成形性を向上する。し
かしてFe含有量を0.15〜1.0%と限定したのは
、0.15%未満では効果が十分でなく、1.0%を越
えると材料の耐食性を低下するためである。Fe refines the crystal grains of the core material and improves formability. However, the reason why the Fe content is limited to 0.15 to 1.0% is that if it is less than 0.15%, the effect will not be sufficient, and if it exceeds 1.0%, the corrosion resistance of the material will decrease.
CuはAl−Cu系、Al −Cu−Mg系の微細な析
出物を生じ、ろう付け加熱後の強度向上に寄与すると共
に、材料の電位を貴にして耐食性を向上させる。しかし
てCu含有量を04〜1.0%と限定したのは、0.4
%未満ではその効果が十分でなく、1.0%を越えると
成形性を低下させ、更にろう付け加熱時に溶融する恐れ
が生じるためである。Cu forms Al-Cu-based and Al-Cu-Mg-based fine precipitates, which contributes to improving the strength after brazing heating, and also increases the potential of the material to improve corrosion resistance. However, the reason why the Cu content was limited to 0.4% to 1.0% was 0.4%.
If the content is less than 1.0%, the effect will not be sufficient, and if it exceeds 1.0%, the moldability will deteriorate and there is a risk of melting during brazing heating.
Mnは強度を向上させるも、その含有量を0.5〜1.
2%と限定したのは、0.5%未満ではその効果が十分
でなく、1.2%を越えると鋳造時に巨大な金属間化合
物を生じ、材料の延性を低下させるためである。Although Mn improves strength, its content should be reduced from 0.5 to 1.
The reason why it is limited to 2% is that if it is less than 0.5%, the effect is not sufficient, and if it exceeds 1.2%, a huge intermetallic compound is generated during casting, which reduces the ductility of the material.
Mgはろう付け加熱によりマトリ・ソクス中に固溶し、
強度を向上させ、更にろう付け加熱後の冷却時及び冷却
後の室温放置時に、Siと共にMg2Siの微細な析出
物を生じて強度を向上する。しかしてMg含有量を0.
05〜0.8%と限定したのは、0.05%未満ではそ
の効果が十分でな(,0,8%を越えるとろう付け性が
低下するためである。Mg is solid dissolved in Matri Soxu by brazing heating,
The strength is improved, and the strength is further improved by forming fine precipitates of Mg2Si together with Si during cooling after brazing heating and when left at room temperature after cooling. However, the Mg content was reduced to 0.
The reason why the content is limited to 0.05 to 0.8% is because the effect is insufficient if it is less than 0.05% (and if it exceeds 0.8%, the brazing properties are reduced).
Cr、Zr、Hf、Ti、Bは材料の組成を均一にし、
材料強度を向上させる効果があり、また不溶性化合物の
析出による粒界周辺の電位差の緩和により耐食性を向上
する。しかしてCr 0.001〜0.5%、 Z
r 0.001〜O13%Hf0.001〜1.5%、
T0.001〜0.5%、B0.0001〜0.1%
の範囲内で、何れか1種又は2種以上を含むように限定
したのは、何れも下限未満では効果が十分でなく、上限
を越えると鋳造時に粗大金属間化合物を生じ、芯材の延
性を低下するためである。Cr, Zr, Hf, Ti, and B make the composition of the material uniform,
It has the effect of improving material strength, and also improves corrosion resistance by relaxing the potential difference around grain boundaries due to the precipitation of insoluble compounds. However, Cr 0.001-0.5%, Z
r0.001~O13%Hf0.001~1.5%,
T0.001~0.5%, B0.0001~0.1%
If the lower limit is less than the lower limit, the effect will not be sufficient, and if the upper limit is exceeded, coarse intermetallic compounds will be formed during casting, and the ductility of the core material will be reduced. This is to reduce the
本発明は上記組成からなる芯材の少なくとも片面にSi
5%以上含むAl合金ろう材をクラッドしたもので、A
l合金ろう材のSi含有量を5%以上と限定したのは、
5%未満では液相線温度が高く、十分なろう付けが困難
となるためである。通常ろう材としてはSiを5〜15
%含有するものが使用され、更にはろう付け性改善の目
的でBe、Bi、Mg等を少量添加する場合もある。ろ
う材は芯材の片面又は両面に、それぞれ全板厚の3〜3
0%、好ましくは3〜15%の範囲でクラッドする。The present invention provides Si on at least one side of the core material having the above composition.
Clad with Al alloy brazing filler metal containing 5% or more, A
The reason why the Si content of the l-alloy brazing filler metal is limited to 5% or more is because
This is because if it is less than 5%, the liquidus temperature will be high and sufficient brazing will be difficult. Usually the brazing filler metal contains 5 to 15 Si.
% of Be, Bi, Mg, etc. may be added for the purpose of improving brazing properties. The brazing filler metal is applied to one or both sides of the core material, each 3 to 3 times the total thickness of the core material.
0% cladding, preferably in the range of 3-15%.
また本発明は上記組成の芯材の片面に、Si5%以上を
含むAl合金ろう材をクラットし、その反対側の面に、
芯材より50m V以上卑な電位を有するAl合金皮材
をクラッドすることができる。これは芯材より卑な電位
を有するAl合金皮材をクラッドすることにより、この
合金層を陰極防食における犠牲層として作用させ、その
芯材を保護するものである。しかしてその電位差を50
mV以上卑としたのは、50mV未満では十分な効果が
得られないためである。尚この犠牲層は全板厚の1〜2
0%、好ましくは2〜10%の範囲でクラッドするとよ
い。In addition, the present invention is characterized by crating an Al alloy brazing material containing 5% or more of Si on one side of the core material having the above composition, and on the other side,
It is possible to clad an Al alloy skin material having a potential 50 mV or more more base than the core material. This is to protect the core material by cladding with an Al alloy skin material having a more base potential than the core material, so that this alloy layer acts as a sacrificial layer in cathodic protection. However, the potential difference is 50
The reason why mV or higher is selected is that a sufficient effect cannot be obtained at less than 50 mV. This sacrificial layer is 1~2 of the total board thickness.
The cladding is preferably 0%, preferably in the range of 2 to 10%.
次に本発明の冷却条件設定の理由について説明する。ろ
う付け加熱(600℃)を行なった際に、Si、Mg、
Cu等がマトリックス中に固溶する。この状態から急冷
すると、Mg25IやAl −Cu系化合物などが微細
に析出してくることにより、強度を向上する。しかして
冷却条件を500℃から200℃まで150℃/min
以上の冷却速度としたのは、この温度範囲で冷却速度が
150℃/minより遅くなると、析出物か粗大化して
しまい、強度向上効果が得られないためである。Next, the reason for setting the cooling conditions of the present invention will be explained. When brazing heating (600℃), Si, Mg,
Cu etc. are dissolved in the matrix. When rapidly cooled from this state, Mg25I, Al--Cu compounds, etc. are finely precipitated, thereby improving the strength. Therefore, the cooling conditions were changed from 500℃ to 200℃ at 150℃/min.
The reason for setting the cooling rate above is that if the cooling rate is slower than 150° C./min in this temperature range, the precipitates will become coarse and the strength improvement effect will not be obtained.
ある。be.
以下本発明を実施例について説明する。 The present invention will be described below with reference to Examples.
実施例−1
第1表に示す組成の合金をDC鋳造により厚さ70 m
m 、幅300 mmの鋳塊とし、これを片面3mmず
つ面削し、580℃で3時間均質化処理を施した後、そ
の両面に4004合金ろう材を片面につき全板厚の15
%となるようにクラッドし熱間圧延と冷間圧延により厚
さ10胴の板とした。これを400℃て2時間焼鈍処理
を施してブレージングシートを作製した。尚第1表中T
は3003合金。Example-1 An alloy having the composition shown in Table 1 was cast to a thickness of 70 m by DC casting.
An ingot with a width of 300 mm and a width of 300 mm was milled on each side, homogenized at 580°C for 3 hours, and then 4004 alloy brazing filler metal was applied on both sides to 15 mm of the total plate thickness on each side.
%, and was hot-rolled and cold-rolled into a plate having a thickness of 10 mm. This was annealed at 400° C. for 2 hours to produce a brazing sheet. In addition, T in Table 1
is 3003 alloy.
Uは6061合金を示す。U indicates 6061 alloy.
このブレージングシートについて、ろう付け加熱後の機
械的性質及びろう付け性の評価を行なった。その結果を
第2表に示す。This brazing sheet was evaluated for mechanical properties and brazing properties after heating for brazing. The results are shown in Table 2.
機械的性質はそれぞれろう付けを模して600℃に加熱
後、冷却速度を変えて冷却し、これを室温に1日、 3
0日、 100日放置した後、測定した。ろう付け性
は第1図(イ)(ロ)に示すように幅30 mm 、長
さ50mmの3003合金板(2)の中央部に、幅30
nun 、長さ50mmのブレージングシート(1)
を一端に直径3n++nのステンレス線(2)を介在さ
せて、垂直に固定し、これを前処理後フルオロアルミン
酸カリウム塩からなるフラックス懇濁液を塗布し、乾燥
後N2ガス雰囲気中610℃で5分間ろう付け加熱し、
第1図(0)に示するう材の間隙充填長さ(I)を測定
した。この試験において間隙充填長さ15IIl111
以上を良と判定した。Mechanical properties were determined by heating to 600°C to simulate brazing, cooling at different cooling rates, and returning to room temperature for 1 day.
After being left for 0 and 100 days, measurements were taken. As shown in Figure 1 (a) and (b), the brazing property was determined by placing a 30 mm wide plate in the center of a 3003 alloy plate (2) with a width of 30 mm and a length of 50 mm.
nun, 50mm long brazing sheet (1)
was fixed vertically with a stainless steel wire (2) with a diameter of 3n++n interposed at one end, and after pretreatment, a flux suspension consisting of potassium fluoroaluminate salt was applied, and after drying, it was heated at 610°C in an N2 gas atmosphere. Heat brazing for 5 minutes,
The gap filling length (I) of the filler material shown in FIG. 1 (0) was measured. In this test, the gap filling length was 15IIl111
The above was judged as good.
実施例−2
第1表に示す組成の合金を実施例−1と同様にしてDC
鋳造により厚さ70mm、幅3 Q Ommの鋳塊とし
、これを片面3mmずつ面削して580℃で3時間均質
化処理を施した後、その片面に4004合金ろう材を反
対面に皮材として7072合金をそれぞれ全板厚の10
%となる様にクラッドし、熱間圧延と冷間圧延により厚
さ1.5mmの仮とした。Example-2 An alloy having the composition shown in Table 1 was subjected to DC treatment in the same manner as in Example-1.
An ingot with a thickness of 70 mm and a width of 3 Q Omm was obtained by casting, and this was faceted by 3 mm on each side and homogenized at 580°C for 3 hours, after which a 4004 alloy brazing filler metal was applied to one side and a skin material was applied to the other side. 7072 alloy as 10 of the total plate thickness.
%, and was hot-rolled and cold-rolled into a tentative material with a thickness of 1.5 mm.
これを400℃で2時間焼鈍処理を施してブレージング
シートを作製した。This was annealed at 400° C. for 2 hours to produce a brazing sheet.
このブレージングシートについてエリクセン試験を行な
って成形性を評価した。またこのブレージングシートを
ラジェーター用ヘッダー材に加工し、3003合金を芯
材とし、4004合金ろう材と7072合金皮材をクラ
ッドした板厚0.4mmのチューブ材と組合せ、ろう付
けを行なってラジェーターとし、これに腐食液を循環さ
せ1.2゜3ケ月毎にヘッダーの30点の孔食深さを測
定し、最大孔食深さを求めた。これ等の結果を第3表に
示す。This brazing sheet was subjected to an Erichsen test to evaluate its moldability. In addition, this brazing sheet was processed into a header material for a radiator, which was combined with a 0.4 mm thick tube material made of 3003 alloy as a core material and clad with 4004 alloy brazing material and 7072 alloy skin material, and then brazed to form a radiator. A corrosive liquid was circulated through this, and the pitting depth was measured at 30 points on the header every 1.2°3 months to determine the maximum pitting depth. These results are shown in Table 3.
試験は腐食液にCl−195ppm、 SO42−6
QppmF e ” 311ppm、 Cu 2+l
ppmを用い、90℃に8時間保持した後、室温に16
時間保持することを繰返して行なった。The test included Cl-195ppm and SO42-6 in the corrosive liquid.
QppmF e ” 311ppm, Cu 2+l
ppm and kept at 90°C for 8 hours, then heated to room temperature for 16 hours.
The holding time was repeated.
第1表乃至第3表から明らかなように本発明方法Nα9
〜18.Nα3θ〜39.Nα59〜68.Nα80〜
89によるものは何れもろう付け性と成形性が良好で従
来合金T、 Uを用いた比較方法Nα28.29゜4
9、 50.78. 79.99. 100と比較し、
ろう付け加熱後の引張強さと耐食性が優れていることが
判る。As is clear from Tables 1 to 3, the method of the present invention Nα9
~18. Nα3θ~39. Nα59-68. Nα80~
89 had good brazeability and formability, and the comparison method using conventional alloys T and U was Nα28.29°4.
9, 50.78. 79.99. compared to 100,
It can be seen that the tensile strength and corrosion resistance after brazing heating are excellent.
これに対し本発明用合金の組成範囲内(A。On the other hand, within the composition range of the alloy for the present invention (A.
F)であっても、冷却速度が150℃/minより遅い
比較方法Nα1. 2. 5. 6ではろう付け加熱後
の強度の改善が不十分であることが判る。また本発明用
合金の組成範囲より外れる比較合金に、L、M、N、0
.P、0.R,Sを用いた比較方法Nα19〜27.4
0〜48.69〜77、90〜98ではろう付け加熱時
に溶融したり、成形性が劣ったり、ろう付け加熱後・の
強度、耐食性の一つ以上が劣ることが判る。F), the comparative method Nα1. has a cooling rate lower than 150° C./min. 2. 5. It can be seen that in No. 6, the improvement in strength after brazing heating was insufficient. In addition, comparative alloys outside the composition range of the alloy for the present invention include L, M, N, 0
.. P, 0. Comparison method using R, S Nα19-27.4
0-48, 69-77, 90-98, it can be seen that it melts during brazing heating, has poor formability, and is poor in one or more of the strength and corrosion resistance after brazing heating.
このように本発明によれば、ろう付け加熱後における強
度が高く、耐食性も良好で、熱交換器の製造において、
熱交換器の薄肉軽量化を可能にする等工業上顕著な効果
を奏するものである。As described above, according to the present invention, the strength after brazing heating is high, the corrosion resistance is also good, and in the production of a heat exchanger,
This has significant industrial effects, such as making it possible to make heat exchangers thinner and lighter.
第1図(()、 (0)はろう付け加熱における間隙充
填試験方法を示すもので、(イ)はろう付け前の側面図
、(0)はろう付け後の側面図、第2図はドロンカップ
タイプのエバポレーターの一例を一部切欠いて示す斜視
図、第3図はラジェータの一例を一部切欠いて示す斜視
図である。
(11ブレージングシート
(2+ 3003合金板
(3) ステンレス線
(4)、 (4)プレート成形体
(5) 冷媒通路
(6) フィン
(7) チューブ
(8座板
(9) バッキング
(10) 樹脂製タンク
(イ)
第
C口)
第2図
第3図Figure 1 ((), (0) shows the gap filling test method during brazing heating, (a) is a side view before brazing, (0) is a side view after brazing, and Figure 2 is a side view after brazing. FIG. 3 is a perspective view showing an example of a radiator with a part cut away. (11 Brazing sheet (2 + 3003 alloy plate (3) Stainless steel wire (4) ), (4) Plate molded body (5) Refrigerant passage (6) Fin (7) Tube (8 seat plate (9) Backing (10) Resin tank (A) Port C) Figure 2 Figure 3
Claims (2)
0wt%。 Cu0.4〜1.0wt%、Mn0.5〜1.2wt%
、Mg0.05〜0.8wt%を含み、更にCr0.0
01〜0.5wt%、Zr0.001〜0.3wt%、
Hf0.001〜1.5wt%、Ti0.001〜0.
5wt%、B0.0001〜0.1wt%の範囲内で何
れか1種又は2種以上を含み、残部Alと不可避的不純
物からなる合金を芯材とし、その片面又は両面にSi5
wt%以上を含むAl合金ろう材をクラッドしたブレー
ジングシートを、熱交換器部材に使用して熱交換器を組
合せ、ろう付け温度に加熱保持後、500℃から200
℃まで150℃/min以上の速度で冷却することを特
徴とするアルミニウム製熱交換器の製造方法。(1) Si0.4-1.2wt%, Fe0.15-1.
0wt%. Cu0.4-1.0wt%, Mn0.5-1.2wt%
, contains Mg0.05-0.8wt%, and further contains Cr0.0
01-0.5wt%, Zr0.001-0.3wt%,
Hf0.001-1.5wt%, Ti0.001-0.
5 wt%, B0.0001 to 0.1 wt%, the core material is an alloy containing one or more types within the range of 0.0001 to 0.1 wt%, and the balance is Al and unavoidable impurities, and one or both sides of the alloy are Si5
A brazing sheet clad with an Al alloy brazing filler material containing more than wt% is used as a heat exchanger member, the heat exchanger is assembled, and after heating and holding at the brazing temperature, it is heated from 500℃ to 200℃.
A method for manufacturing an aluminum heat exchanger, characterized in that the aluminum heat exchanger is cooled down to a temperature of 150°C/min or more.
0wt%、Cu0.4〜1.0wt%、Mn0.5〜1
.2wt%、Mg0.05〜0.8wt%を含み、更に
Cr0.001〜0.5wt%、Zr0.001〜0.
3wt%、Hf0.001〜1.5wt%、Ti0.0
01〜0.5wt%、B0.0001〜0.1wt%の
範囲内で何れか1種又は2種以上を含み、残部Alと不
可避的不純物からなる合金を芯材とし、その片面にSi
5wt%以上を含むAl合金ろう材をクラッドし、反対
面に芯材より50mV以上卑な電位を有するAl合金皮
材をクラッドしたブレージングシートを、熱交換器部材
に使用して熱交換器を組合せ、ろう付け温度に加熱後、
500℃から200℃まで150℃/min以上の速度
で冷却することを特徴とするアルミニウム製熱交換器の
製造方法。(2) Si0.4-1.2wt%, Fe0.15-1.
0wt%, Cu0.4-1.0wt%, Mn0.5-1
.. 2wt%, Mg0.05-0.8wt%, and further contains Cr0.001-0.5wt%, Zr0.001-0.
3wt%, Hf0.001-1.5wt%, Ti0.0
The core material is an alloy containing one or more of the following in the range of 0.01 to 0.5 wt% and B0.0001 to 0.1 wt%, with the remainder being Al and unavoidable impurities.
A heat exchanger is assembled by using a brazing sheet clad with an Al alloy brazing material containing 5 wt% or more and an Al alloy skin material having a potential 50 mV or more more base than the core material on the opposite side as a heat exchanger member. , after heating to brazing temperature,
A method for manufacturing an aluminum heat exchanger, characterized by cooling from 500°C to 200°C at a rate of 150°C/min or more.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP13037889A JPH038569A (en) | 1989-05-24 | 1989-05-24 | Production of heat exchanger made of aluminum |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP13037889A JPH038569A (en) | 1989-05-24 | 1989-05-24 | Production of heat exchanger made of aluminum |
Publications (1)
Publication Number | Publication Date |
---|---|
JPH038569A true JPH038569A (en) | 1991-01-16 |
Family
ID=15032913
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP13037889A Pending JPH038569A (en) | 1989-05-24 | 1989-05-24 | Production of heat exchanger made of aluminum |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPH038569A (en) |
Cited By (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH04371368A (en) * | 1991-06-19 | 1992-12-24 | Nippon Light Metal Co Ltd | Brazing sheet having excellent corrosion resistance and production thereof |
JPH0547590A (en) * | 1991-08-21 | 1993-02-26 | Murata Mfg Co Ltd | Laminated electronic component |
WO1999055925A1 (en) * | 1998-04-29 | 1999-11-04 | Corus Aluminium Walzprodukte Gmbh | Aluminium alloy for use in a brazed assembly |
WO2007133286A3 (en) * | 2006-04-21 | 2008-12-18 | Alcoa Inc | Multilayer braze-able sheet |
WO2014157116A1 (en) * | 2013-03-29 | 2014-10-02 | 株式会社神戸製鋼所 | Brazed structure |
-
1989
- 1989-05-24 JP JP13037889A patent/JPH038569A/en active Pending
Cited By (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH04371368A (en) * | 1991-06-19 | 1992-12-24 | Nippon Light Metal Co Ltd | Brazing sheet having excellent corrosion resistance and production thereof |
JPH0547590A (en) * | 1991-08-21 | 1993-02-26 | Murata Mfg Co Ltd | Laminated electronic component |
WO1999055925A1 (en) * | 1998-04-29 | 1999-11-04 | Corus Aluminium Walzprodukte Gmbh | Aluminium alloy for use in a brazed assembly |
US6413331B1 (en) | 1998-04-29 | 2002-07-02 | Corus Aluminium Walzprodukte Gmbh | Aluminium alloy for use in a brazed assembly |
WO2007133286A3 (en) * | 2006-04-21 | 2008-12-18 | Alcoa Inc | Multilayer braze-able sheet |
US7749613B2 (en) | 2006-04-21 | 2010-07-06 | Alcoa Inc. | Multilayer braze-able sheet |
WO2014157116A1 (en) * | 2013-03-29 | 2014-10-02 | 株式会社神戸製鋼所 | Brazed structure |
JP2014198892A (en) * | 2013-03-29 | 2014-10-23 | 株式会社神戸製鋼所 | Brazed joint structure |
CN105074026A (en) * | 2013-03-29 | 2015-11-18 | 株式会社神户制钢所 | Brazed structure |
US10369665B2 (en) | 2013-03-29 | 2019-08-06 | Kobe Steel, Ltd. | Brazed structure |
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