CN105861888A - Al-Si-Er alloy of wide Si-composition window for high-temperature-resisting brazing aluminum/steel composite strip - Google Patents
Al-Si-Er alloy of wide Si-composition window for high-temperature-resisting brazing aluminum/steel composite strip Download PDFInfo
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- CN105861888A CN105861888A CN201610238024.XA CN201610238024A CN105861888A CN 105861888 A CN105861888 A CN 105861888A CN 201610238024 A CN201610238024 A CN 201610238024A CN 105861888 A CN105861888 A CN 105861888A
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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
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
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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
- C22F1/043—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 silicon as the next major constituent
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- Heat Treatment Of Sheet Steel (AREA)
Abstract
The invention discloses an Al-Si-Er alloy of a wide Si-composition window for a high-temperature-resisting brazing aluminum/steel composite strip, and belongs to the technical field of alloy materials. According to the composition proportion of an aluminum alloy material for machining the high-temperature-resisting brazing aluminum/steel composite strip, Er with the mass percent of 0.075 +/-0.01% is added into an aluminum substrate containing Si with the mass percent of 0.25% to 0.99%; the aluminum alloy with the above composition proportion can effectively restrain generation of interfacial compounds during high-temperature brazing, and the Si-composition window with the good interface bonding under the 550 DEG C 3h annealing and brazing simulation condition is widened; and the problems that in actual production, an aluminum/steel interface generates brittle intermetallic compounds, and the composition window is small can be solved.
Description
Technical field
The wide Si that the present invention relates to a kind of high temperature resistant brazed aluminum/steel composite strip becomes split window
Al-Si-Er alloy, belongs to technical field of alloy material.
Technical background
Aluminum density is low, corrosion-resistant, heat conduction is good, and hardness of steel is high, price is low and has excellent toughness,
Aluminum/steel layer shape composite strip combines both premium properties, is for thermal power generation air cooling system
The critical material of system fin.The alloy matrix aluminum being conventionally used to processing aluminum/steel composite band is more
Use 1050 aluminium alloys.But 1050 aluminium alloys and steel plate carry out being combined, anneal, under high temperature
When soldering processes, aluminum/steel compound interface is easily generated Al-Fe frangible compounds, thus reduces aluminum
The boundary strength of/steel composite band.There are some researches show that aluminum side addition Si can press down in aluminum/steel composite band
The generation of interfacial brittle compound during preparing high-temp soldering.
According to current technique, aluminum/steel layer shape composite strip aluminum side in patent CN104962789A
Rafifinal is used to add the Si of 0.41wt.%-0.63wt.% to suppress aluminum/steel layer shape composite strip interface
The generation of Al-Fe frangible compounds.In actual production process, Si composition interval is little, and serious forgiveness is low,
Accurately control difficulty big, probe into and there is the aluminium alloy of wider Si composition range there is important work
Industry meaning.
There are some researches show that again aluminum side adds micro alloying element Er and can change aluminum/steel layer shape composite band
The thickness of compound, pattern and distribution between material interface metal, therefore become at wider Si aluminum side
Er is additionally added on the basis of point scope, multiple for high temperature resistant brazed aluminum/steel to obtaining one
The wide Si of crossed belt material becomes the Al-Si-Er alloy of split window, solves aluminum/steel interface in actual production
Produce brittle intermetallic thing and become the problems such as split window is little.
Summary of the invention
It is an object of the invention to by aluminum side containing Si aluminium alloy adds a small amount of Er element
The method of (0.075 ± 0.01wt.%), widens Si and becomes split window.Play Si, Er element to exist
Effect between Fe, Al, prepares a kind of aluminum for processing high temperature resistant brazed aluminum/steel composite band
Alloy.
Its technical scheme is such, adds a small amount of Si, Er element in aluminum substrate,
The generation of interface compound between ferro-aluminum can be suppressed when aluminum/steel composite band annealing and soldering, subtract
Few interfacial brittle phase, thus improve ferro-aluminum interface bond strength.
A kind of wide Si for high temperature resistant brazed aluminum/steel composite strip becomes the Al-Si-Er of split window
Alloy, it is characterised in that the mass percent of Si is in aluminum alloy side, aluminium alloy
The mass percent of 0.25～0.99%, Er is 0.075 ± 0.01%, and surplus is aluminum and inevitable
Impurity.
Wherein steel is 08Al steel.
The preparation method of aluminium alloy described above, it is characterised in that comprise the following steps:
Smelting temperature is at 790 ± 10 DEG C, is first melted by aluminium ingot, is subsequently added Al-Si intermediate alloy,
After intermediate alloy melts, hexachlorethane degasification, stirring, insulation stands a period of time, makes to melt
Swage casting is carried out after each elementary composition is evenly distributed in body.
Total deformation is carried out with 08Al steel after the aluminium alloy of mentioned component is rolled into aluminium foil by the present invention
Amount is the cold rolling Combined Processing of 60%, then spreads at 520 DEG C of diffusion annealing 21h or 550 DEG C
Annealing 3h, 520 DEG C of annealing 21h are for analog composite band aluminum steel circle under normarzing annealing technique
Face is become metallurgical binding from mechanical engagement, and 550 DEG C of 3h are uneven in order to simulate furnace temperature in factory
Even meeting is no makes band lose efficacy.
Brazed aluminum that the present invention is high temperature resistant/steel composite strip is used for the high temperature brazing of 625 DEG C.The present invention
Simulation soldering processes, and experiment uses 30min to rise to 625 DEG C of insulation 10min from room temperature
The simulation soldering of rear air cooling processes, to ensure the high temperature resistant application of material.By observing boundary
Face situation, Al-Si-Er/ steel composite band of the present invention can be used for high temperature resistant soldering application, interface
Do not produce brittle intermetallic thing, overcome the problem that prior art bond strength is low.
With common add Si aluminium alloy compared with, the present invention uses the one of mentioned component proportioning to use
In the aluminium alloy of processing high temperature resistant brazed aluminum/steel composite band, 550 DEG C of 3h annealing and mould are widened
Intend the Si that interface cohesion is good in the case of soldering and become split window, effectively suppression high temperature brazing time circle
The generation of face compound.
Accompanying drawing explanation
Fig. 1: Al-0.99Si-0.075Er/ steel 520 DEG C 21h annealing and simulation soldering process rear interface；
Fig. 2: Al-0.79Si-0.076Er/ steel 520 DEG C 21h annealing and simulation soldering process rear interface；
Fig. 3: Al-0.62Si-0.074Er/ steel 520 DEG C 21h annealing and simulation soldering process rear interface；
Fig. 4: Al-0.39Si-0.077Er/ steel 520 DEG C 21h annealing and simulation soldering process rear interface；
Fig. 5: Al-0.25Si-0.076Er/ steel 520 DEG C 21h annealing and simulation soldering process rear interface；
Fig. 6: Al-0.074Er/ steel 520 DEG C 21h annealing and simulation soldering process rear interface；
Fig. 7: Al-0.99Si/ steel 520 DEG C 21h annealing and simulation soldering process rear interface；
Fig. 8: Al-0.83Si/ steel 520 DEG C 21h annealing and simulation soldering process rear interface；
Fig. 9: Al-0.63Si/ steel 520 DEG C 21h annealing and simulation soldering process rear interface；
Figure 10: Al-0.41Si/ steel 520 DEG C 21h annealing and simulation soldering process rear interface；
Figure 11: Al-0.25Si/ steel 520 DEG C 21h annealing and simulation soldering process rear interface；
The 520 DEG C of 21h annealing of Figure 12: rafifinal/steel and simulation soldering process rear interface.
Figure 13: Al-0.99Si-0.075Er/ steel 550 DEG C 3h annealing and simulation soldering process rear interface；
Figure 14: Al-0.79Si-0.076Er/ steel 550 DEG C 3h annealing and simulation soldering process rear interface；
Figure 15: Al-0.62Si-0.074Er/ steel 550 DEG C 3h annealing and simulation soldering process rear interface；
Figure 16: Al-0.39Si-0.077Er/ steel 550 DEG C 3h annealing and simulation soldering process rear interface；
Figure 17: Al-0.25Si-0.076Er/ steel 550 DEG C 3h annealing and simulation soldering process rear interface；
Figure 18: Al-0.074Er/ steel 550 DEG C 3h annealing and simulation soldering process rear interface；
Figure 19: Al-0.99Si/ steel 550 DEG C 3h annealing and simulation soldering process rear interface；
Figure 20: Al-0.83Si/ steel 550 DEG C 3h annealing and simulation soldering process rear interface；
Figure 21: Al-0.63Si/ steel 550 DEG C 3h annealing and simulation soldering process rear interface；
Figure 22: Al-0.41Si/ steel 550 DEG C 3h annealing and simulation soldering process rear interface；
Figure 23: Al-0.25Si/ steel 550 DEG C 3h annealing and simulation soldering process rear interface；
The 550 DEG C of 3h annealing of Figure 24: rafifinal/steel and simulation soldering process rear interface.
Detailed description of the invention
Below in conjunction with embodiment, the present invention will be further described, but the present invention is not limited to following
Embodiment.
Use graphite crucible melting and iron mould casting to prepare alloy cast ingot, raw materials used for rafifinal,
The intermediate alloy of Al-21wt.%Si and Al-6wt.%Er.At smelting temperature is 790 ± 10 DEG C,
First aluminium ingot is melted, be subsequently added Al-Si and Al-Er intermediate alloy, treat that intermediate alloy melts
After, hexachlorethane degasification, stirring, after insulation stands, make each elementary composition distribution in melt equal
Swage casting is carried out after even.It is prepared for the alloy of kind of heterogeneity, is recorded in fact by XRF
Border composition, as shown in table 1 below.
Carry out with steel after the aluminium alloy of preparation is rolled into aluminium foil deflection be about 60% cold rolling multiple
Conjunction processes, and carries out recrystallization annealing process+simulation soldering heat treatment subsequently.Aluminum/steel is cold rolling compound
After, crystal grain gross distortion, cold rolling composite band plasticity declines, composite band is carried out 520 DEG C/21h
Or 550 DEG C/3h annealing heat treatment, to meet following process needs；Experiment use 30min from
After room temperature to 625 DEG C insulation 10min, the simulation soldering of air cooling processes to ensure the resistance to of material
High temperature is applied.
Table 1 technic metal composition
Aluminum prepared by the aluminium alloy in embodiment 1:A1/steel composite band in 520 DEG C of 21h annealing and
Simulation soldering processes rear interface and does not produce interface compound, in conjunction with all right, sees Fig. 1.
Aluminum prepared by the aluminium alloy in embodiment 2:A2/steel composite band in 520 DEG C of 21h annealing and
Simulation soldering processes rear interface and does not produce interface compound, in conjunction with all right, sees Fig. 2.
Aluminum prepared by the aluminium alloy in embodiment 3:A3/steel composite band in 520 DEG C of 21h annealing and
Simulation soldering processes rear interface and does not produce interface compound, in conjunction with all right, sees Fig. 3.
Aluminum prepared by the aluminium alloy in embodiment 4:A4/steel composite band in 520 DEG C of 21h annealing and
Simulation soldering processes rear interface and does not produce interface compound, in conjunction with all right, sees Fig. 4.
Aluminum prepared by the aluminium alloy in embodiment 5:A5/steel composite band in 520 DEG C of 21h annealing and
Simulation soldering processes rear interface and does not produce interface compound, in conjunction with all right, sees Fig. 5.
Aluminum prepared by the aluminium alloy in comparative example 1:A6/steel composite band in 520 DEG C of 21h annealing and
Simulation soldering processes rear interface and occurs in that the frangible compounds of discontinuously distribution, sees Fig. 6, reduces boundary
The bond strength in face, easily causes matrix steel band to separate with cladding aluminium strip.
Aluminum prepared by the aluminium alloy in comparative example 2:A7/steel composite band in 520 DEG C of 21h annealing and
Simulation soldering processes rear interface and does not produce interface compound, in conjunction with all right, sees Fig. 7.
Aluminum prepared by the aluminium alloy in comparative example 3:A8/steel composite band in 520 DEG C of 21h annealing and
Simulation soldering processes rear interface and does not produce interface compound, in conjunction with all right, sees Fig. 8.
Aluminum prepared by the aluminium alloy in comparative example 4:A9/steel composite band in 520 DEG C of 21h annealing and
Simulation soldering processes rear interface and does not produce interface compound, in conjunction with all right, sees Fig. 9.
Aluminum prepared by the aluminium alloy in comparative example 5:A10/steel composite band is annealed at 520 DEG C of 21h
And simulation soldering processes rear interface and do not produces interface compound, in conjunction with all right, see figure
10。
Aluminum prepared by the aluminium alloy in comparative example 6:A11/steel composite band is annealed at 520 DEG C of 21h
And simulation soldering processes rear interface and do not produces interface compound, in conjunction with all right, see figure
11。
Aluminum prepared by the aluminium alloy in comparative example 7:A12/steel composite band is annealed at 520 DEG C of 21h
And simulation soldering processes rear interface and occurs in that the brittle interface compound of a large amount of continuous distribution, see figure
12, it is substantially reduced the bond strength at interface, easily causes matrix steel band to separate with cladding aluminium strip.
Aluminum prepared by the aluminium alloy in embodiment 6:A1/steel composite band in 520 DEG C of 3h annealing and
Simulation soldering processes rear interface and does not produce interface compound, in conjunction with all right, sees Figure 13.
Aluminum prepared by the aluminium alloy in embodiment 7:A2/steel composite band in 520 DEG C of 3h annealing and
Simulation soldering processes rear interface and does not produce interface compound, in conjunction with all right, sees Figure 14.
Aluminum prepared by the aluminium alloy in embodiment 8:A3/steel composite band in 520 DEG C of 3h annealing and
Simulation soldering processes rear interface and does not produce interface compound, in conjunction with all right, sees Figure 15.
Aluminum prepared by the aluminium alloy in embodiment 9:A4/steel composite band in 520 DEG C of 3h annealing and
Simulation soldering processes rear interface and does not produce interface compound, in conjunction with all right, sees Figure 16.
Aluminum prepared by the aluminium alloy in embodiment 10:A5/steel composite band in 520 DEG C of 3h annealing and
Simulation soldering processes rear interface and does not produce interface compound, in conjunction with all right, sees Figure 17.
Aluminum prepared by the aluminium alloy in comparative example 8:A6/steel composite band in 550 DEG C of 3h annealing and
Simulation soldering processes rear interface and occurs in that the brittle interface compound of discontinuously distribution, sees Figure 18,
Reduce the bond strength at interface, easily cause matrix steel band to separate with cladding aluminium strip.
Aluminum prepared by the aluminium alloy in comparative example 9:A7/steel composite band in 550 DEG C of 3h annealing and
Simulation soldering processes rear interface and does not produce interface compound, in conjunction with all right, sees Figure 19.
Aluminum prepared by the aluminium alloy in comparative example 10:A8/steel composite band in 550 DEG C of 3h annealing and
Simulation soldering processes rear interface and does not produce interface compound, in conjunction with all right, sees Figure 20.
Aluminum prepared by the aluminium alloy in comparative example 11:A9/steel composite band in 550 DEG C of 3h annealing and
Simulation soldering processes rear interface and does not produce interface compound, in conjunction with all right, sees Figure 21.
Aluminum prepared by the aluminium alloy in comparative example 12:A10/steel composite band is annealed at 550 DEG C of 3h
And simulation soldering processes rear interface and do not produces interface compound, in conjunction with all right, see figure
22。
Aluminum prepared by the aluminium alloy in comparative example 13:A11/steel composite band is annealed at 550 DEG C of 3h
And simulation soldering processes rear interface and occurs in that the brittle interface compound of a large amount of continuous distribution, see figure
23, it is substantially reduced the bond strength at interface, easily causes matrix steel band to separate with cladding aluminium strip.
Aluminum prepared by the aluminium alloy in comparative example 14:A12/steel composite band is annealed at 550 DEG C of 3h
And simulation soldering processes rear interface and occurs in that the brittle interface compound of a large amount of continuous distribution, see figure
24, it is substantially reduced the bond strength at interface, easily causes matrix steel band to separate with cladding aluminium strip.
From Figure 12 and 24, rafifinal/steel composite band is moved back at 520 DEG C of 21h or 550 DEG C of 3h
Fire and simulation soldering process rear interface and all occur in that the average thickness of a large amount of stratiform continuous distribution about
It is the brittle interface compound of 8 μm, is substantially reduced the bond strength at interface.
From Fig. 6 and 18, Al-0.074Er/ steel composite band at 520 DEG C of 21h or 550 DEG C of 3h
Annealing and simulation soldering process rear interface and the most all occur in that the average thickness of discontinuously distribution is about 5
μm brittle interface compound, the bond strength at interface can not meet use requirement.
From Fig. 7～11, Al-0.25～0.99Si/ steel composite band at 520 DEG C of 21h annealing and mould
Intending soldering process rear interface and do not observe interface compound, interface cohesion is all right.
But from Figure 19～23, Al-0.41～0.99Si/ steel composite band in 550 DEG C of 3h annealing and simulation
Soldering processes rear interface and does not observe interface compound, and interface cohesion is all right,
And Al-0.25～0.41Si/ steel composite band processes rear interface in 550 DEG C of 3h annealing and simulation soldering and goes out
The average thickness having showed continuous distribution is about 10 μm brittle interface compounds, reduces interface
Bond strength.Therefore, only Al-0.41～0.99Si/ steel composite band is 520 DEG C of 21h or 550 DEG C
3h annealing and simulation soldering process rear interface and do not observe interface compound, interface
In conjunction with all right.
Existed from Fig. 1～5 and Figure 13～17, Al-0.25～0.99Si-0.075Er/ steel composite band
Boundary is not the most observed at after 520 DEG C of 21h or 550 DEG C of 3h heat treatments and simulation soldering process interface
The existence of face compound, interface cohesion is all right.With can be at 520 DEG C of 21h or 550 DEG C of 3h
Annealing and simulation soldering process Al-0.41～the 0.99Si/ steel composite band phase that rear interface is well combined
Ratio, has widened the one-tenth split window of Si.
In sum, the aluminum for processing high temperature resistant brazed aluminum/steel composite band that the present invention uses
The composition proportion of alloy material is at the aluminum substrate that the mass percent containing Si is 0.25～0.99%
Middle interpolation mass percent is the Er of 0.075 ± 0.01%.Use mentioned component proportioning aluminum close
Gold, can effectively suppress the generation of interface compound during high temperature brazing, 520 DEG C of 21h or 550 DEG C
3h anneals and simulates soldering process rear interface and do not observes interface compound, interface
In conjunction with all right, and it is good to have widened interface cohesion in the case of 550 DEG C of 3h anneal and simulate soldering
Good Si becomes split window.The present invention can solve aluminum in actual production/steel interface and produce brittle metal
Between compound with become the problems such as split window is little.
Claims (5)
1. the wide Si for high temperature resistant brazed aluminum/steel composite strip becomes the Al-Si-Er of split window to close
Gold, it is characterised in that the mass percent of Si is in aluminum alloy side, aluminium alloy
The mass percent of 0.25～0.99%, Er is 0.075 ± 0.01%, and surplus is aluminum and can not keep away
The impurity exempted from.
2. comprise the high temperature resistant brazed aluminum/steel composite strip of Al-Si-Er alloy described in claim 1,
It is characterized in that, wherein steel is 08Al steel.
3. comprise the high temperature resistant brazed aluminum/steel composite strip of Al-Si-Er alloy described in claim 1
Application, it is characterised in that the aluminium alloy of claim 1 composition is rolled into after aluminium foil with 08Al
Steel carries out the cold rolling Combined Processing that total deformation is 60%, then at 520 DEG C of diffusion annealing 21h or
Diffusion annealing 3h at 550 DEG C.
4. comprise the high temperature resistant brazed aluminum/steel composite band of Al-Si-Er alloy described in claim 1
The application of material, it is characterised in that for the high temperature brazing of 625 DEG C.
5. the high temperature resistant brazed aluminum/steel composite strip of the Al-Si-Er alloy described in claim 3 should
With, it is characterised in that carry out the high temperature brazing of 625 DEG C after annealing again.
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201610238024.XA CN105861888B (en) | 2016-04-17 | 2016-04-17 | A kind of wide Si for high temperature resistant brazed aluminum/steel composite strip at split window Al-Si-Er alloys |
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| CN201610238024.XA CN105861888B (en) | 2016-04-17 | 2016-04-17 | A kind of wide Si for high temperature resistant brazed aluminum/steel composite strip at split window Al-Si-Er alloys |
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Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2010209445A (en) * | 2009-03-12 | 2010-09-24 | Furukawa-Sky Aluminum Corp | Brazing sheet of highly heat-resistant aluminum alloy and method for manufacturing the same |
| US20120129003A1 (en) * | 2010-09-21 | 2012-05-24 | Furukawa-Sky Aluminum Corp. | High-strenght aluminum alloy brazing sheet and method of manufacture |
| CN103882269A (en) * | 2014-03-24 | 2014-06-25 | 北京工业大学 | Aluminum alloy material for high-temperature-resistant brazing aluminum/steel composite strip and application of aluminum alloy material |
| CN104801878A (en) * | 2015-04-22 | 2015-07-29 | 北京工业大学 | High-temperature-resistant braze welding brazing aluminum/connecting aluminum/steel three-layer composite plate |
| CN104962789A (en) * | 2015-05-22 | 2015-10-07 | 北京工业大学 | Aluminium alloy material used for preparing high temperature resistant brazed aluminium/steel composite sheet material prepared from aluminium-silicon brazing filler metal, and preparation method thereof |
-
2016
- 2016-04-17 CN CN201610238024.XA patent/CN105861888B/en active Active
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2010209445A (en) * | 2009-03-12 | 2010-09-24 | Furukawa-Sky Aluminum Corp | Brazing sheet of highly heat-resistant aluminum alloy and method for manufacturing the same |
| US20120129003A1 (en) * | 2010-09-21 | 2012-05-24 | Furukawa-Sky Aluminum Corp. | High-strenght aluminum alloy brazing sheet and method of manufacture |
| CN103882269A (en) * | 2014-03-24 | 2014-06-25 | 北京工业大学 | Aluminum alloy material for high-temperature-resistant brazing aluminum/steel composite strip and application of aluminum alloy material |
| CN104801878A (en) * | 2015-04-22 | 2015-07-29 | 北京工业大学 | High-temperature-resistant braze welding brazing aluminum/connecting aluminum/steel three-layer composite plate |
| CN104962789A (en) * | 2015-05-22 | 2015-10-07 | 北京工业大学 | Aluminium alloy material used for preparing high temperature resistant brazed aluminium/steel composite sheet material prepared from aluminium-silicon brazing filler metal, and preparation method thereof |
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