CN1973056B - Method for producing aluminum alloy brazing sheet and aluminum alloy brazing sheet - Google Patents
Method for producing aluminum alloy brazing sheet and aluminum alloy brazing sheet Download PDFInfo
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- CN1973056B CN1973056B CN2005800167564A CN200580016756A CN1973056B CN 1973056 B CN1973056 B CN 1973056B CN 2005800167564 A CN2005800167564 A CN 2005800167564A CN 200580016756 A CN200580016756 A CN 200580016756A CN 1973056 B CN1973056 B CN 1973056B
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/053—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with zinc as the next major constituent
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/10—Alloys based on aluminium with zinc as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/14—Alloys based on aluminium with copper as the next major constituent with silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/16—Alloys based on aluminium with copper as the next major constituent with magnesium
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- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
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- Crystallography & Structural Chemistry (AREA)
- Laminated Bodies (AREA)
- Details Of Heat-Exchange And Heat-Transfer (AREA)
- Continuous Casting (AREA)
Abstract
The invention relates to a process for producing an Al-Mn alloy sheet with improved liquid film migration resistance when used as core alloy in brazing sheet, comprising the steps of: casting an ingot having a composition comprising (in weight percent): 0.5 < Mn <= 1.7 0.06<Cu<=1.5 Si <= 1.3 Mg <= 0.25 Ti < 0.2 Zn <= 2.0 Fe <= 0.5 at least one element of the group of elements consisting of 0.05 <Zr <=0.25 and 0.05 < Cr<=0.25 other elements < 0.05 each and total <0.20, balance Al. homogenisation and preheat hot rolling . cold rolling (including intermediate anneals whenever required), and wherein the homogenisation temperature is at least 450 DEG C for a duration of at least 1 hour followed by an air cooling at a rate of at least 20 DEG C/h and wherein the pre-heat temperature is at least 400 DEG C for at least 0.5 hour.
Description
The present invention relates to a kind of method of the Al-Mn of production alloy sheets, this alloy sheets has the anti-liquid film migration of raising as the core alloy in the brazing sheet material time.The invention still further relates to the Al-Mn alloy sheets of producing according to described method, and the use of described alloy sheets.
In soldering was used, the phenomenon that is called as " liquid film migration " or LFM can cause the deterioration of the overall performance of brazing product such as vaporizer, scatterer, heating air box (heater core) etc.Term in the document " LFM " is also referred to as " core dissolving " or " core infiltration " and " core erosion ".Here we use term " LFM " to refer to all these specific terms.Although cause LFM really cutter system also and imperfectly understand as if exist a certain amount of dislocation can increase the seriousness of LFM in the core alloy of brazing sheet.Be known that with the soft attitude of same material or slight cold working state and compare that fully the material behind annealing (0 state) and strain hardening and/or the stress relieving state (for example H14, H24 etc.) is relative low to the susceptibility of LFM.By term " slight cold working ", we refer to for example punching press of commercial run, roll forming or the distortion that tension leveled produced, these processing typical case is used to produce the assembly of heat exchanger, for example vaporizer or oil cooler central layer (oilcooler core plate), folded tube etc.When the brazing sheet to core alloy and Al-Si clad alloy formation is out of shape to form product and then to carry out the soldering circulation time, find that a spot of distortion is enough to cause the LFM of brazing sheet.If LFM is excessive in the expansion of core alloy, then solderability, intensity and erosion resistance can reduce.Be known that for example chromium, zirconium and vanadium can improve susceptibility to LFM to the alloying element that postpones recrystallize.Therefore it is also known that the manganese dispersoid particle also can postpone recrystallize and improve susceptibility to LFM.The amount of manganese dispersoid particle and size depend on the machining path of brazing sheet.
Use for soldering, the core alloy of brazing sheet product need have the combination of good intensity and formability.Obviously, the susceptibility to LFM must be in fully low level to guarantee having enough erosion resistances and braze ability.Can obtain higher intensity by carrying out alloying with element such as silicon, manganese, chromium, zirconium or vanadium.Yet these alloying elements have also improved the susceptibility to LFM.For example H14 state or H24 state reduce susceptibility to LFM also to have advised using non-0 state.Yet,, usually damaged the formability of brazing sheet product although these states can effectively reduce LFM.The for example slight cold deformation processing of other alternative method is as tension levelling, or the use of non-recrystallize upper layer is unmanageable in the scale operation practice, so may damage reproducibility and/or formability.
An object of the present invention is to provide the method for producing the Al-Mn alloy sheets, this alloy sheets has the anti-liquid film migration of raising when being used as the core alloy of brazing sheet, wherein this alloy has the combination of good intensity/formability and also has fully low LFM susceptibility and enough erosion resistances.
Another purpose provides the method for producing described Al-Mn alloy sheets, and this method is easy to control and produces reproducible product.
Another purpose of the present invention provides the Al-Mn alloy sheets that having in folded tube, vaporizer or oil cooler central layer, the cooling fin blank (fin stock) etc. improved anti-liquid film migration, and wherein said alloy has the combination of good intensity/formability and also has fully low LFM susceptibility, good braze ability and enough erosion resistances.
According to the present invention, use the method for producing the Al-Mn alloy sheets that as brazing sheet core alloy the time, has the anti-liquid film migration of raising to realize one or more described purposes, this method comprises the steps:
● casting comprises the composition (% meter by weight) of following composition:
0 0.5＜Mn≤1.7, preferred 0.6-1.7,
0 0.06＜Cu≤1.5, preferred 0.2-1.5,
Zero Si≤1.3, preferred Si≤0.8, more preferably Si≤0.3,
○Mg≤0.25
○Ti＜0.2
○Zn≤2.0
○Fe≤0.5
The zero at least a element that is selected from 0.05＜Zr≤0.25 and 0.05＜Cr≤0.25
Zero other element every kind＜0.05 and total amount＜0.20, surplus is Al.
● homogenize and preheat
● hot rolling
● cold rolling (comprising the process annealing when needing)
Wherein homogenization temperature is at least 450 ℃ and continue at least 1 hour, then carries out air cooling with the speed of at least 20 ℃/h, and wherein pre-heating temperature is at least 400 ℃ and continues at least 0.5 hour.
The conventional production technology of use such as DC casting or continuous casting is cast.
The method according to this invention can be produced a kind of Al-Mn alloy, and this Al-Mn alloy not only has the combination of good intensity/formability but also have fully low LFM susceptibility and enough erosion resistances when being used as the core alloy of brazing sheet.The inventor is unexpected to be found, although it is reported owing to the delayed effect of chromium to alloy recrystallization, therefore chromium has disadvantageous effect to LFM susceptibility, but the chemical constitution of described alloy and the combination of machined parameters particularly homogenize and the process that preheats can produce and has fully low LFM susceptibility and thereby product with enough erosion resistances.Contain Cr and/or contain the precipitate of Zr owing to form, can reduce susceptibility LFM with being combined in of processing conditions forms in the alloy.Also reinforced alloys of chromium in addition, and the recrystallize of alloy causes enough formabilities.The inventor finds can obtain similar result by V alloyization or by V to the combined alloyization of Cr and/or Zr.
In embodiments of the invention, Cr and/or Zr content are at least 0.08%.The inventor finds when the chromium content of use 0.08% or 0.08% zirconium content or its combination at least at least, when combining with above-mentioned processing condition, produces higher-strength and enough anti-LFM combinations.
In embodiments of the invention, maximum Mg content is 0.1%, and preferred maximum Mg content is 0.05%.Mg content should hang down as far as possible to avoid the harmful effect of magnesium to the flux that uses in the controlled atmosphere brazing process.In embodiments of the invention, copper content is 0.7-1.2%.
In one embodiment of the invention, manganese content is 0.7-1.4%.If manganese content surpasses 1.4%, can increase the difficulty in the preparation, and if be lower than 0.7% then the undercapacity of alloy.In one embodiment of the invention, maximum zinc content is preferably 0.4% to prevent the excessively anodizing in some applications of core alloy.In embodiments of the invention, iron level preferably is lower than 0.35% to prevent forming compound between nonconforming big ferrous metal in industrial casting operation process.
In embodiments of the invention, homogenization temperature is about 530-620 ℃, preferred 530-595 ℃, preferred lasting 1-25 hour, more preferably continue 10-16 hour, and wherein pre-heating temperature is about 400～530 ℃, is preferably 420-510 ℃, preferred lasting 1-25 hour, more preferably continue 1-10 hour.In alloy according to the present invention, when temperature and time of in given scope, selecting to homogenize and pre-warmed temperature and time, found to have preferably between intensity, formability, LFM susceptibility and the erosion resistance and taken into account, and when processing alloy, obtained noticeable especially taking into account according to above-mentioned preferred temperature and time.
It is known to those skilled in the art that annealed time and temperature independently do not select usually.The metallurgical process that great majority are relevant is thermal activation, causes the combination of the time of high temperature and weak point may have the situation of identical result with lesser temps and long period.
The method according to this invention also is included in is being enough to make the Al-Mn alloy to carry out recrystallization annealing under the combination of the annealing temperature-annealing time of perfect recrystallization basically after cold rolling.Under this condition, obtain the highest formability.
In one embodiment of the invention, the maximum silicone content of Al-Mn alloy is 0.3 weight %.In a preferred embodiment of the invention, the maximum silicone content of Al-Mn alloy is 0.15 weight %.Known silicon can increase the susceptibility to LFM.Therefore, select alap silicone content.Yet the inventor finds to be at most 0.3% when using, when preferably being at most 0.15% silicone content, the suitable combination of acquisition LFM susceptibility and intensity.
In one embodiment of the invention, Cr≤0.18%, preferably at least 0.06%, more preferably 0.08%＜Cr≤0.15%, more preferred 0.08%＜Cr≤0.12%.When Cr content surpassed 0.18%, because the formation of big intermetallic compound, it is very difficult that the casting of Al-Mn alloy becomes.Casting Cr content is lower than 0.15% or be lower than 0.12 Al-Mn and can not have problems.By adding at least 0.08% Cr, its combination to the influence of LFM susceptibility and above-mentioned processing condition causes the appropriate combination of LFM susceptibility and intensity.Form and being combined in the precipitate that forms in the alloy and can reducing susceptibility of processing condition LFM.In one embodiment of the invention, this method one side at least of also being included in the Al-Mn alloy is with AA4000～series or optionally comprise that the Al-Si brazing alloy of the highest 2.0%Zn coats.Can or cast by for example roll bond or any other known technology such as spray coating and coat.
The present invention also is embodied in the plate of producing according to method mentioned above, wherein unit elongation is at least 18% before the soldering, preferably at least 19%, more preferably at least 21%, and/or n～value before at least 0.270 the soldering, and/or 140MPa, preferred tensile strength after the soldering of 150MPa at least at least.On 80mm specification length, measure unit elongation, also represent with A80.
In one embodiment of the invention, when testing according to ASTM G85 A3, the sample SWAAT life-span is at least 15 days after the soldering that records in aperture time of fate, and being preferably at least 20 days does not have perforation.Low LFM susceptibility is reflected in the erosion resistance of the raising in the moulding heat exchanger component after the soldering.
In one embodiment of the invention, in folded tube or be used for application under the simulated condition, with above-mentioned plate as the core in the brazing sheet, this brazing sheet has or does not have non brazing lining or water side lining (waterside liner) alloy such as AA7072, AA1145 or AA3005, perhaps contains the Al-Mn type alloy of Zn amount for 0.5-5.0%, preferred 0.5-2.5%.For the application of plate, as utilize application in the heat exchanger of folded tube as the core in the brazing sheet, relevant especially for the requirement of intensity, formability, LFM susceptibility and erosion resistance.
Be especially suitable for use as core alloy in the brazing sheet material according to the panel material of aforesaid method production, this brazing sheet material intention is used to make the parts of pipe plate fin type heat exchanger, for example scatterer, heating air box and condenser, perhaps be used to make the parts of plate fin type heat exchanger, for example vaporizer or oil cooler central layer or radiator tank or heating air box are especially suitable for use as the core alloy in the soldering cooling fin blank that is intended to the manufacturing heat exchanger component.
Now specific embodiments of the present invention will be described by following non-limiting example.
The alloy embodiment that table 1. is produced according to the invention
| Alloy | Cu | Fe | Si | Mn | Mg | Ti | Cr | Zr |
| 1 (reference) | 0.76 | 0.18 | 0.10 | 1.14 | 0.03 | 0.13 | ＜0.01 | ＜0.01 |
| 2 | 0.80 | 0.21 | 0.09 | 1.15 | 0.05 | 0.13 | 0.05 | 0.05 |
| 3 | 0.78 | 0.21 | 0.09 | 1.20 | 0.03 | 0.13 | 0.11 | ＜0.01 |
| 4 | 0.78 | 0.20 | 0.08 | 1.16 | 0.02 | 0.12 | 0.15 | ＜0.01 |
| 5 | 0.72 | 0.20 | 0.07 | 1.21 | 0.01 | 0.14 | 0.08 | ＜0.01 |
| 6 | 0.76 | 0.15 | 0.08 | 1.19 | 0.01 | 0.12 | 0.06 | ＜0.01 |
| Standard | 0.5～0.7 | ＜0.5 | ＜0.3 | 0.65-1.0 | ＜0.02 | 0.08～0.10 | - | - |
| Other element every kind＜0.05 and total amount＜0.20, surplus are Al | ||||||||
Under differing temps, these alloys (alloy 1-4) are homogenized processing and lasting different time.Use the both sides of AA4045 clad alloy subsequently, each side is 10% of thickness, be preheating of the differing temps of before hot rolling, carrying out and different time subsequently, hot rolling is arrived 6.5mm subsequently 350 ℃ of following process annealings 3 hours, first is cold rolled to 2.3mm, then once more 350 ℃ of following process annealings 3 hours, and second final size that is cold rolled to 0.5mm.Alloy is carried out recrystallization annealing to be handled to promote recrystallize substantially completely.In order to test the LFM behavior, with material extending 2-10%.Use and show that the most deep penetrating draw level is used for the LFM data of table 2.
Use the both sides of AA4045 clad alloy 5 and 6, each side is 10% of thickness, and preheats before hot rolling subsequently, and hot rolling is to 3.5mm then, is cold rolled to 0.41mm and does not carry out process annealing.After cold rolling, material carried out recrystallization annealing handle to promote recrystallize substantially completely.Test the LFM behavior in a manner described.The result is as shown in table 2.The alloy of called after " standard " is to be used for the crucial alloy of using of LFM-.
In table 2:
● "+/～" expression penetrates 50～60% core alloy thickness;
● "+" expression penetrates 30～50% core alloy thickness;
● " ++ " expression penetrates＜30% core alloy thickness.
Because unit elongation demonstrates big dispersion usually, therefore can use the substituting index of n～value as formability.With regard to the minimum strength of 140MPa requires at least, the formability that n～value representation of at least 0.270 is good.When comparing with the standard alloy that is used for the crucial application of LFM, according to alloy of the present invention, for example the alloy 2-6 in the table 2 provides equal LFM performance, but has significantly higher soldering back draft performance.
Alloy embodiment (2-4,5) and comparative alloy (1) that table 2. is produced according to the invention
(n.d.=undetermined)
| Alloy | Homogenize ℃/h | Preheat ℃/h | Before the soldering | After the soldering | The sample SWAAT fate of boring a hole | Anti-LFM * | ||
| A80％ | The n-value | 0.2PS MPa | UTS MPa | |||||
| 12333333346 standards | 610/8610/8610/8610/8610/24580/12580/12550/12550/12610/8610/10610/10 | 430/24430/24490/24490/2430/24430/5490/2490/24490/2430/24430/1430/1 | 17.4 21.2 19.4 19.4 21.7 19.5 22.2 18.6 24.5 21.1 24.0 n.d. n.d. | 0.264 0.276 0.296 0.286 O.285 0.300 0.304 0.307 0.300 0.277 0.282 n.d. n.d. | 60 69 63 66 61 68 62 66 65 70 61 n.d. 50 | 133 152 155 152 153 156 152 157 159 153 155 n.d. 130 | 26 38 ＞40 ＞40 ＞40 37 35 22 29 33 24 n.d. n.d. | +/- + + + + + ++ + ++ ++ ++ ++ ++ |
Can use the another kind of specific alloy of producing according to the inventive method to have following compositing range, in weight %:
● Si 0.8-1.0, and typical case about 0.9
● Fe 0.25-0.4, and typical case about 0.35
● Cu 0.25-0.45, and typical case about 0.40
● Mn 0.55-0.9, and typical case about 0.85
● Mg 0.1-0.22, and typical case about 0.15
● Zn 0.06-0.10, and typical case about 0.08
● Cr 0.06-0.10, and typical case about 0.08
● Zr 0.06-0.10, and the typical case is about 0.08,
● the aluminium of surplus and unavoidable impurities.
Wherein this alloy can be used for tube sheet, side support and upper water box (header tank).
What certainly can understand is that the present invention is not restricted to above-mentioned embodiment and embodiment, and comprises specification sheets and following interior any and all embodiments of claims scope.
Claims (22)
1. produce the method for Al-Mn alloy sheets, this Al-Mn alloy sheets has the anti-liquid film migration of raising when being used for the core alloy of brazing sheet, and this method may further comprise the steps:
The composition that casting is grouped into by following one-tenth, weight %:
○0.5＜Mn≤1.7
○0.06＜Cu≤1.5
○0＜Si≤0.15
○Mg＜0.05
○Ti＜0.2
○Zn≤2.0
○0＜Fe≤0.5
○0.05＜Cr≤0.25
Zero other element every kind＜0.05, and total amount＜0.20, the Al of surplus,
Homogenize and preheat
Hot rolling
Have the cold rolling of optional process annealing, and
Wherein homogenization temperature is at least 450 ℃ and continues at least 1 hour, then carries out air cooling with the speed of at least 20 ℃/h, and wherein pre-heating temperature is at least 400 ℃ and continues at least 0.5 hour.
2. according to the process of claim 1 wherein that homogenization temperature is 530-620 ℃ and continues 1-25 hour, and wherein pre-heating temperature is 400-530 ℃ and continues 1-25 hour.
3. according to the method for claim 1 or 2, wherein Mn is 0.7-1.4%.
4. according to the process of claim 1 wherein Cr≤0.18.
5. according to the process of claim 1 wherein 0.08＜Cr≤0.15.
6. according to the process of claim 1 wherein 0.08＜Cr≤0.12.
7. according to the process of claim 1 wherein Zn≤0.4%.
8. according to the method for claim 1, also comprise with optional comprising the one side at least that the Al-Si brazing alloy of the highest 2.0%Zn coats the Al-Mn alloy.
9. according to the method for claim 1, also comprise the one side at least that coats the Al-Mn alloy with the Al-Si brazing alloy, this Al-Si brazing alloy is optional to be comprised the highest 2.0%Zn and has in the non brazing lining alloy or Zn content is the Al-Mn type alloy of 0.5-5.0%.
10. according to the method for claim 1, also comprise the one side at least that coats the Al-Mn alloy with the Al-Si brazing alloy, this Al-Si brazing alloy is optional to be comprised the highest 2.0%Zn and has in the non brazing lining alloy or Zn content is the Al-Mn type alloy of 0.5-2.5%.
11. according to the method for claim 9 or 10, lining alloy is AA7072 or AA1145 or AA3005 in the wherein said non brazing.
12. according to the plate that the method for claim 1 is produced, wherein unit elongation is at least 18% before the soldering.
13. according to the plate that the method for claim 1 is produced, wherein unit elongation is at least 19% before the soldering.
14. according to the plate of claim 12, wherein tensile strength is at least 140MPa after the soldering.
15. according to the plate of claim 14, wherein tensile strength is at least 150MPa after the soldering.
16. according to the plate of claim 12, wherein the n-value is at least 0.270 before the soldering.
17. according to the plate of claim 12, wherein when testing according to ASTM G85 A3, the SWAAT life-span of welding back sample is at least 15 days and not perforation.
18. the plate of producing according to the method for claim 1 or according to the plate of claim 12 purposes as the core alloy of brazing sheet, this brazing sheet intention is used to prepare the parts of pipe plate fin type heat exchanger.
19. according to the purposes of claim 18, the parts of wherein said pipe plate fin type heat exchanger are scatterer, heating air box and condenser.
20. the plate of producing according to the method for claim 1 or according to the plate of claim 12 purposes as brazing sheet core alloy, this brazing sheet intention is used to prepare the parts of plate fin type heat exchanger.
21. according to the purposes of claim 20, the parts of wherein said plate fin type heat exchanger are vaporizer or oil cooler central layer or radiator tank or heating air box.
22. the plate of producing according to the method for claim 1 or according to the plate of claim 12 purposes as the core alloy of soldering cooling fin blank, this soldering cooling fin blank intention is used to prepare the parts of heat exchanger.
Applications Claiming Priority (7)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| EP04076545 | 2004-05-26 | ||
| EP04076545.5 | 2004-05-26 | ||
| EP04076785.7 | 2004-06-18 | ||
| EP04076785 | 2004-06-18 | ||
| EP04077623 | 2004-09-23 | ||
| EP04077623.9 | 2004-09-23 | ||
| PCT/EP2005/005751 WO2005118899A1 (en) | 2004-05-26 | 2005-05-25 | Process for producing an aluminium alloy brazing sheet, aluminium alloy brazing sheet |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN1973056A CN1973056A (en) | 2007-05-30 |
| CN1973056B true CN1973056B (en) | 2010-11-24 |
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN2005800167564A Expired - Lifetime CN1973056B (en) | 2004-05-26 | 2005-05-25 | Method for producing aluminum alloy brazing sheet and aluminum alloy brazing sheet |
Country Status (8)
| Country | Link |
|---|---|
| EP (1) | EP1753885B2 (en) |
| JP (1) | JP5326123B2 (en) |
| KR (1) | KR101216246B1 (en) |
| CN (1) | CN1973056B (en) |
| CA (1) | CA2565978C (en) |
| HU (1) | HUE032303T2 (en) |
| MX (1) | MXPA06013571A (en) |
| WO (1) | WO2005118899A1 (en) |
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| CN101798645B (en) * | 2010-04-17 | 2012-01-04 | 上海交通大学 | Aluminum alloy for heat exchanger fins and preparation method thereof |
| JP5737798B2 (en) * | 2010-07-08 | 2015-06-17 | 三菱アルミニウム株式会社 | Aluminum alloy brazing sheet excellent in strength and formability and method for producing the same |
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- 2005-05-25 CN CN2005800167564A patent/CN1973056B/en not_active Expired - Lifetime
- 2005-05-25 EP EP05746552.8A patent/EP1753885B2/en not_active Expired - Lifetime
- 2005-05-25 MX MXPA06013571A patent/MXPA06013571A/en active IP Right Grant
- 2005-05-25 CA CA2565978A patent/CA2565978C/en not_active Expired - Lifetime
- 2005-05-25 WO PCT/EP2005/005751 patent/WO2005118899A1/en not_active Ceased
- 2005-05-25 HU HUE05746552A patent/HUE032303T2/en unknown
- 2005-05-25 JP JP2007513822A patent/JP5326123B2/en not_active Expired - Lifetime
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| US4761267A (en) * | 1986-03-31 | 1988-08-02 | Sky Aluminium Co., Ltd. | Aluminum alloy for use as core of clad material |
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Also Published As
| Publication number | Publication date |
|---|---|
| HUE032303T2 (en) | 2017-09-28 |
| WO2005118899A1 (en) | 2005-12-15 |
| EP1753885A1 (en) | 2007-02-21 |
| JP5326123B2 (en) | 2013-10-30 |
| KR101216246B1 (en) | 2012-12-28 |
| CN1973056A (en) | 2007-05-30 |
| EP1753885B1 (en) | 2016-12-28 |
| EP1753885B2 (en) | 2022-08-24 |
| KR20070058383A (en) | 2007-06-08 |
| MXPA06013571A (en) | 2007-03-15 |
| CA2565978A1 (en) | 2005-12-15 |
| JP2008500453A (en) | 2008-01-10 |
| CA2565978C (en) | 2013-03-26 |
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