CN113103688B - High-temperature-resistant brazing aluminum/steel composite plate capable of inhibiting interface compounds - Google Patents
High-temperature-resistant brazing aluminum/steel composite plate capable of inhibiting interface compounds Download PDFInfo
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- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B15/00—Layered products comprising a layer of metal
- B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
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- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
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- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/38—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling sheets of limited length, e.g. folded sheets, superimposed sheets, pack rolling
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- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
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- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/38—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling sheets of limited length, e.g. folded sheets, superimposed sheets, pack rolling
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Abstract
A high temperature resistant brazing aluminum/steel composite plate for inhibiting interface compounds belongs to the technical field of alloy materials. The Si content in the aluminum side alloy used for processing the high-temperature-resistant brazing aluminum/steel composite strip is 0.26-0.88 wt.%, and the Si content in the iron side alloy is 0.13-0.82 wt.%. The aluminum-silicon alloy and the iron-silicon alloy which adopt the component proportion can effectively inhibit the generation of interface compounds during high-temperature brazing, improve the interface bonding strength and widen the Si component window with good interface bonding under the conditions of 520 ℃/36h annealing and simulated brazing. The invention can solve the problems of small windows of Er and Si components on the aluminum side in the actual production of the aluminum/steel composite plate and the like.
Description
Technical Field
The invention relates to Al-Si and Fe-Si alloys for a group of high-temperature-resistant brazing aluminum/steel composite plates, belonging to the technical field of alloy materials.
Technical Field
At present, most important heat dissipation materials of thermal power generation air cooling systems adopt aluminum/steel composite materials, the advantages of low aluminum density, good heat conduction, high steel strength, low price and the like are integrated, 1050 aluminum alloy is adopted on the aluminum side which is traditionally used for processing the aluminum/steel composite strip, 08Al steel is adopted on the steel side, and the main problem is that Al-Fe brittle compounds are easily generated on the aluminum/steel composite interface when the 1050 aluminum alloy and a steel plate are subjected to subsequent annealing and brazing treatment at high temperature, and the interface bonding strength of the aluminum/steel composite strip is reduced. It has been found that the addition of Si to the aluminum side of an aluminum/steel composite strip suppresses the formation of interfacial brittle compounds during high temperature brazing, but this is not satisfactory.
In patent CN102321834A, the addition of 0.7-0.9wt.% of Si, 0.075 ± 0.01wt.% of Er and patent CN104962789A in high purity aluminum effectively suppresses the generation of interfacial hard brittle intermetallic compounds during high temperature brazing of aluminum/steel composite strip. At present, si and Er alloy needs to be added on an aluminum side in a related process, the Si and Er component intervals need to be accurately controlled in the actual production process, the fault tolerance rate is low, and the research on the Si adding on an iron side and the Si component range wider on the aluminum side has important industrial significance.
Disclosure of Invention
The invention aims to simultaneously add a small amount of Si (0.13-0.82 wt.%) and a small amount of Si (0.26-0.88 wt.%) to the iron side and the aluminum side of a high-temperature-resistant brazing aluminum/steel composite plate to inhibit intermediate compounds, widen the Si component window on the aluminum side, and fully play the roles of the Si on the Fe side and the Al side to prepare the aluminum/iron composite plate for processing high-temperature-resistant brazing.
According to the technical scheme, a small amount of Si element is added on the iron side and the aluminum side respectively, so that the generation of interface compounds between aluminum and iron is effectively inhibited during annealing and brazing of the aluminum/iron composite plate, and interface brittle phases are reduced, thereby improving the bonding strength of the aluminum-iron interface.
A high-temperature-resistant brazing aluminum/steel composite sheet material with suppressed interface compounds, characterized in that a small amount of Si element is added to the iron side and a small amount of Si element is added to the aluminum side, the mass percent of Si on the aluminum side is 0.26 to 0.88%, the balance being aluminum and unavoidable impurities, the mass percent of Si on the iron side is 0.13 to 0.82%, and the balance being iron and unavoidable impurities.
The preparation method of the aluminum-silicon alloy comprises the following steps: at the smelting temperature of 790 +/-10 ℃, firstly melting an aluminum ingot, then adding an Al-Si intermediate alloy, degassing by using hexachloroethane after the intermediate alloy is melted, stirring, preserving heat and standing for a period of time, and carrying out iron mold casting after all element components in the melt are uniformly distributed.
The preparation method of the iron-silicon alloy comprises the following steps: melting a pure iron ingot in a vacuum melting furnace at the melting temperature of 1650 +/-10 ℃, then adding Fe-Si intermediate alloy, stirring uniformly after the intermediate alloy is melted, keeping the temperature and standing for a period of time to ensure that each element component in the melt is uniformly distributed, and then casting by using a steel die.
In the invention, aluminum-silicon alloy and iron-silicon with the components are respectively rolled into an aluminum plate and an iron plate, then cold rolling composite treatment with the total deformation of 50 percent is carried out, and then diffusion annealing is carried out for 36 hours at 520 ℃ so as to meet the requirement of subsequent deformation processing.
The high-temperature-resistant brazing aluminum/steel composite plate is used for high-temperature brazing at 610 ℃. The simulated brazing treatment is carried out by air cooling after the temperature is increased from room temperature to 610 ℃ for 10min in 40 min. By observing the interface bonding condition and a peeling test, the material can be ensured to be applied under the high-temperature condition.
When the mass percent of Si on the iron side is 0.82 and the mass percent of Si on the aluminum side is 0-0.88 (and is not 0), the interface bonding strength is greater than the tensile strength of the matrix on the aluminum side; when the mass percent of Si on the iron side is 0.13 and the mass percent of Si on the aluminum side is 0.26-0.88, the interface bonding strength is greater than the tensile strength of the matrix on the aluminum side; when the iron side is pure iron and the mass percent of Si on the aluminum side is 0-0.88, the interface peel strength is only 1-2.5N/mm.
When the mass percent of Si on the iron side is 0.82 and the mass percent of Si on the aluminum side is 0.46-0.88, no intermetallic compound appears on the interface, and the interface bonding state is good; when the mass percent of Si on the iron side is 0.13 and the mass percent of Si on the aluminum side is 0.46-0.88, no intermetallic compound appears on the interface, and the interface bonding state is good; when the iron side is pure iron and the mass percent of Si on the aluminum side is 0-0.88, intermetallic compounds appear on the interface, and the interface bonding is poor.
Compared with the common aluminum/steel composite belt only adding Si on the aluminum side, the invention has the characteristics that the Si component process window on the aluminum side is effectively widened by adding a small amount of Si element on the iron side, so that the fault tolerance rate of industrial production is higher, and the yield of products is higher.
Drawings
FIG. 1: annealing Fe-0.82Si/Al-0.88Si at 520 ℃ for 36h and simulating an interface after brazing treatment;
FIG. 2: an interface is formed after the annealing and the simulated brazing treatment are carried out for 36h at the temperature of 520 ℃ and Fe-0.82 Si/Al-0.66Si;
FIG. 3: annealing at the temperature of 520 ℃ for 36h and simulating an interface after brazing treatment, wherein the interface is Fe-0.82 Si/Al-0.46Si;
FIG. 4: an interface after annealing at the temperature of 520 ℃ for 36h and simulated brazing treatment of Fe-0.82 Si/Al-0.26Si;
FIG. 5 is a schematic view of: annealing Fe-0.82Si/Al at 520 ℃ for 36h and simulating an interface after brazing treatment;
FIG. 6: annealing at 520 ℃ for 36h at Fe-0.13Si/Al-0.88Si and simulating an interface after brazing treatment;
FIG. 7: annealing at the temperature of 520 ℃ for 36h and simulating an interface after brazing treatment at the temperature of Fe-0.13 Si/Al-0.66Si;
FIG. 8: annealing at the temperature of 520 ℃ for 36h and simulating an interface after brazing treatment of Fe-0.13 Si/Al-0.46Si;
FIG. 9: an interface after annealing at 520 ℃ for 36h and simulated brazing treatment of Fe-0.13 Si/Al-0.26Si;
FIG. 10: annealing at 520 ℃ for 36h and simulating an interface after brazing treatment of Fe-0.13 Si/Al;
FIG. 11: annealing at the temperature of Fe/Al-0.88Si of 520 ℃ for 36h and simulating an interface after brazing treatment;
FIG. 12: annealing at the temperature of 520 ℃ for 36h and simulating an interface after brazing treatment of Fe/Al-0.66Si;
FIG. 13: annealing at the temperature of 520 ℃ for 36h and simulating an interface after brazing treatment of Fe/Al-0.46Si;
FIG. 14 is a schematic view of: annealing at the temperature of Fe/Al-0.26Si of 520 ℃ for 36h and simulating an interface after brazing treatment;
FIG. 15 is a schematic view of: annealing at the temperature of 520 ℃ for 36h and simulating an interface after brazing treatment;
FIG. 16: tensile curve of 36h annealing at 520 ℃ of Fe-0.82Si/Al-0.88Si and peeling test after simulated brazing treatment
FIG. 17: tensile curve of strip test after Fe-0.82Si/Al-0.66Si annealing at 520 ℃ for 36h and simulated brazing treatment
FIG. 18: tensile curve of strip test after Fe-0.82Si/Al-0.46Si annealing at 520 ℃ for 36h and simulated brazing treatment
FIG. 19: tensile curve of strip test after Fe-0.82Si/Al-0.26Si annealing at 520 ℃ for 36h and simulated brazing treatment
FIG. 20: tensile curve of peeling test after Fe-0.82Si/Al annealing at 520 ℃ for 36h and simulated brazing treatment
FIG. 21: tensile curve of 36h annealing at 520 ℃ of Fe-0.13Si/Al-0.88Si and peeling test after simulated brazing treatment
FIG. 22: tensile curve of stripping test after Fe-0.13Si/Al-0.66Si annealing at 520 ℃ for 36h and simulated brazing treatment
FIG. 23: tensile curve of stripping test after Fe-0.13Si/Al-0.46Si annealing at 520 ℃ for 36h and simulated brazing treatment
FIG. 24: tensile curve of stripping test after Fe-0.13Si/Al-0.26Si annealing at 520 ℃ for 36h and simulated brazing treatment
FIG. 25: tensile curve of strip test after Fe-0.13Si/Al annealing at 520 ℃ for 36h and simulated brazing treatment
Detailed Description
The present invention will be further illustrated with reference to the following examples, but the present invention is not limited to the following examples.
The alloy ingot is prepared by adopting graphite crucible smelting and iron mold casting, and the used raw materials are high-purity aluminum, pure iron and intermediate alloy of Al-20wt.% Si. At the smelting temperature of 790 +/-10 ℃, firstly melting an aluminum ingot, then adding an Al-Si intermediate alloy, degassing by hexachloroethane after the intermediate alloy is melted, stirring, preserving heat and standing to ensure that each element component in the melt is uniformly distributed, and then carrying out iron mold casting. Aluminum silicon alloys of various compositions were prepared and the actual compositions were measured by XRF, as shown in table 1 below. The preparation method of the iron-silicon alloy comprises the following steps: melting a pure iron ingot in a vacuum melting furnace at the melting temperature of 1650 +/-10 ℃, then adding Fe-Si intermediate alloy, stirring uniformly after the intermediate alloy is melted, keeping the temperature and standing for a period of time to ensure that each element component in the melt is uniformly distributed, and then casting by using a steel die. Iron-silicon alloys of various compositions were prepared and the actual compositions were determined photometrically as shown in table 2 below.
Respectively rolling the prepared aluminum-silicon alloy into an aluminum plate and rolling the prepared iron-silicon alloy into an iron plate, performing cold rolling compounding with the deformation amount of about 50%, and then performing recrystallization annealing and simulated brazing heat treatment. And (3) the plasticity of the cold-rolled composite plate is reduced, the composite plate is subjected to annealing heat treatment at 520 ℃/36h to eliminate stress to meet the requirement of subsequent deformation processing, and the experiment adopts simulated brazing treatment of air cooling after the temperature is raised to 610 ℃ from room temperature for 40min and is kept for 10min to ensure the high-temperature resistance application of the material.
In order to more intuitively evaluate the interface bonding performance, the interface bonding strength needs to be judged by a peel test. Firstly, after a rolled aluminum/iron composite board is leveled, a sample is prepared by adopting linear cutting, the specification of the sample is 100mm (RD) in length and 10mm in width, one end of the sample is selected to be grooved, the depth of the grooved sample is about 10mm, a tearing reserved opening of a peeling test is prepared, the aluminum/iron composite board is convenient to peel off after recrystallization annealing and simulated brazing treatment, then the surface of the sample is cleaned by decontamination, and finally annealing and simulated brazing treatment are carried out. An UTM4304 microcomputer controlled electronic universal tester is selected to detect the mechanical property of interface bonding, the maximum test force is 30kN, the power is 1kW, and the accuracy grade is 0.5.
TABLE 1 Experimental aluminum side alloy compositions
TABLE 2 Experimental iron side alloy compositions
TABLE 3 statistical table of interfacial bonding strength after Fe- (0-0.82) Si/Al- (0-0.88) Si annealing at 520 ℃ for 36h + simulated brazing treatment
Note that: the strength of the aluminum matrix is higher than that of the aluminum matrix, namely, the aluminum matrix is broken under the condition that the interface is not torn when a peeling test is carried out, namely, the interface bonding strength is higher than the tensile strength of the aluminum matrix.
Example 1: the aluminum/iron composite strip prepared in B1/A1 has no interface compound after annealing at 520 ℃ for 36h and simulated brazing treatment, and the bonding condition is good, as shown in figure 1.
Example 2: the aluminum/iron composite strip prepared in B1/A2 has no interface compound generated on the interface after 36h annealing at 520 ℃ and simulated brazing treatment, and the bonding condition is good, as shown in figure 2.
Example 3: the aluminum/iron composite strip prepared in B1/A3 has no interface compound after annealing at 520 ℃ for 36h and simulated brazing treatment, and the bonding condition is good, as shown in figure 3.
Example 4: the aluminum/iron composite strip prepared in B1/A4 produced only a small amount of interfacial compounds at the interface after 36h annealing at 520 ℃ and simulated brazing treatment, see FIG. 4.
Example 5: the aluminum/iron composite strip prepared in B1/A5 produced only very little interfacial compound at the interface after 36h annealing at 520 ℃ and simulated brazing treatment, see FIG. 5.
Example 6: the aluminum/iron composite strip prepared in B2/A1 has no interface compound after annealing at 520 ℃ for 36h and simulated brazing treatment, and the bonding condition is good, as shown in figure 6.
Example 7: the aluminum/iron composite strip prepared in B2/A2 has no interface compound generated on the interface after 36h annealing at 520 ℃ and simulated brazing treatment, and the bonding condition is good, as shown in figure 7.
Example 8: the aluminum/iron composite strip prepared in B2/A3 has no interface compound generated on the interface after 36h annealing at 520 ℃ and simulated brazing treatment, and the bonding condition is good, as shown in figure 8.
Example 9: the aluminum/iron composite strip prepared in B2/A4 generates discontinuous distribution of interface compounds after annealing at 520 ℃ for 36h and simulated brazing treatment, and the interface bonding strength is reduced as shown in figure 9.
Example 10: the aluminum/iron composite strip prepared in B2/A5 generates discontinuous distribution of interface compounds after annealing at 520 ℃ for 36h and simulated brazing treatment, and the interface bonding strength is reduced as shown in figure 10.
Comparative example 1: after the aluminum/iron composite strip prepared in B3/A1 is annealed at 520 ℃ for 36h and subjected to simulated brazing treatment, continuously distributed interface compounds appear on the interface, see figure 11, the bonding strength of the interface is reduced, and the aluminum-iron interface separation is easily caused.
Comparative example 2: after the aluminum/iron composite strip prepared in B3/A2 is annealed for 36h at 520 ℃ and subjected to simulated brazing treatment, continuously distributed interface compounds appear on the interface, see figure 12, the bonding strength of the interface is reduced, and the aluminum-iron interface separation is easily caused.
Comparative example 3: after the aluminum/iron composite strip prepared in B3/A3 is annealed for 36h at 520 ℃ and subjected to simulated brazing treatment, continuous cracking appears on the interface, see figure 13, the bonding strength of the interface is reduced, and the aluminum-iron interface separation is easily caused.
Comparative example 4: after the aluminum/iron composite strip prepared in B3/A4 is annealed at 520 ℃ for 36h and subjected to simulated brazing treatment, continuously distributed interface compounds appear on the interface, see figure 14, the bonding strength of the interface is reduced, and the aluminum-iron interface separation is easily caused.
Comparative example 5: after the aluminum/iron composite strip prepared in B3/A5 is annealed for 36h at 520 ℃ and subjected to simulated brazing treatment, continuously distributed interface compounds appear on the interface, see figure 15, the bonding strength of the interface is reduced, and the aluminum-iron interface separation is easily caused.
As can be seen from FIGS. 11, 12, 13, 14 and 15, the Fe/Al-0.88Si, fe/Al-0.66Si, fe/Al-0.26Si and Fe/Al composite plates have a large number of brittle interface compounds with the average thicknesses of 19 μm, 21 μm, 20 μm and 39 μm, which are continuously distributed in a layered manner, on the interface after the annealing treatment at 520 ℃ for 36h and the simulated brazing treatment, and the Fe/Al-0.46Si composite strip has continuous cracking on the interface after the annealing treatment at 520 ℃ for 36h and the simulated brazing treatment, so that the bonding strength of the interface is greatly reduced.
As can be seen from FIGS. 1 to 3 and 6 to 8, the composite plates of Fe-0.82Si/Al-0.88Si, fe-0.82Si/Al-0.66Si, fe-0.82Si/Al-0.46Si, fe-0.13Si/Al-0.88Si, fe-0.13Si/Al-0.66Si and Fe-0.13Si/Al-0.46Si were annealed at 520 ℃/36 hours and simulated brazing treatment, and no interfacial compound was observed at the interface, and the interface bonding condition was good. As can be seen from FIGS. 4, 5, 9 and 10, the interface of the Fe-0.82Si/Al-0.26Si and Fe-0.82Si/Al composite plates after annealing at 520 ℃ for 36h and simulated brazing treatment is observed to have a small amount of interface compounds, the interface bonding condition is good, and the interface of the Fe-0.13Si/Al-0.26Si and Fe-0.13Si/Al composite plates after annealing at 520 ℃ for 36h and simulated brazing treatment respectively has brittle interface compounds with the average thickness of about 6 μm and 8 μm, which are discontinuously distributed, and may have certain influence on the bonding strength of the interface.
When the composite plate of Fe-0.13Si/Al- (0-0.88 Si) and Fe-0.82Si/Al- (0-0.88 Si) is subjected to a peeling test after annealing at 520 ℃/36h and simulated brazing treatment, the aluminum side matrix is broken under the condition that the interface is not cracked, namely the interface peeling strength is greater than the tensile strength of the aluminum side matrix, and the specific peeling test tensile curve is shown in an attached figure 16-25; when the Fe/Al- (0-0.88 Si) composite plate is subjected to a peeling test after annealing at 520 ℃/36h and simulated brazing treatment, the interfaces can be torn under the action of small tensile force, namely the peeling strength of the interfaces is smaller than that of the aluminum side matrix, and specific statistical data are shown in Table 3.
In conclusion, the aluminum alloy material for processing the high-temperature-resistant brazing aluminum/steel composite plate comprises 0.13-0.82 mass percent of Si added to the iron side and 0.46-0.88 mass percent of Si added to the aluminum side, and the alloy adopting the composition ratio can effectively inhibit the generation of interface compounds during high-temperature brazing, has good interface bonding condition after 520 ℃/36h annealing and simulated brazing treatment, and widens the Si component window with good interface bonding under the conditions of 520 ℃/36h annealing and simulated brazing. The invention can solve the problems of brittle intermetallic compound generated on the aluminum/iron interface, small component window and the like in the practical production.
Claims (5)
1. A high temperature resistant brazing aluminum/steel composite plate for inhibiting interface compounds is characterized in that a small amount of Si element is added on the iron side and a small amount of Si element is added on the aluminum side respectively, the mass percent of Si on the aluminum side is 0.26-0.66%, the balance is aluminum and inevitable impurities, the mass percent of Si on the iron side is 0.13-0.82%, and the balance is iron and inevitable impurities;
respectively rolling aluminum-silicon alloy and iron-silicon into an aluminum plate and an iron plate, and then performing cold rolling composite treatment with total deformation of 50%, wherein the cold rolling composite treatment is characterized in that diffusion annealing is performed for 36 hours at 520 ℃;
the high-temperature-resistant brazing aluminum/steel composite plate is used for high-temperature brazing at the temperature of 610 ℃.
2. The method for preparing the high temperature resistant brazing aluminum/steel composite plate material capable of inhibiting the interface compound according to claim 1, the aluminum-silicon alloy, comprising the following steps: melting an aluminum ingot at the melting temperature of 790 +/-10 ℃, then adding an Al-Si intermediate alloy, degassing and stirring hexachloroethane after the intermediate alloy is melted, preserving heat and standing for a period of time to uniformly distribute each element component in the melt, and then carrying out iron mold casting.
3. The high temperature brazing aluminum/steel composite plate for inhibiting interface compounds as claimed in claim 1, the ferrosilicon alloy preparation method comprises the following steps: in a vacuum smelting furnace, at a smelting temperature of 1650 +/-10 ℃, firstly melting a pure iron ingot, then adding Fe-Si intermediate alloy, after the intermediate alloy is melted, uniformly stirring, keeping the temperature and standing for a period of time to uniformly distribute each element component in the melt, and then casting by a steel die.
4. The high temperature resistant brazing aluminum/steel composite plate with suppressed interfacial compounds as claimed in claim 1, wherein the brazing treatment is performed by air cooling after the temperature is raised from room temperature to 610 ℃ for 10min at 40 min.
5. The high temperature resistant brazing aluminum/steel composite sheet with suppressed interfacial compounds as claimed in claim 1, wherein the interface bonding strength is higher than the tensile strength of the aluminum side matrix when the mass percentage of Si on the iron side is 0.82 and the mass percentage of Si on the aluminum side is 0.26 to 0.66%; when the mass percent of Si on the iron side is 0.13 and the mass percent of Si on the aluminum side is 0.26-0.66%, the interface bonding strength is larger than the tensile strength of the matrix on the aluminum side.
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Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20060275623A1 (en) * | 2005-06-01 | 2006-12-07 | Kabushiki Kaisha Kobe Seiko Sho ( Kobe Steel, Ltd. ) | Steel sheet for dissimilar materials weldbonding to aluminum material and dissimilar materials bonded body |
| CN102066597A (en) * | 2008-06-13 | 2011-05-18 | 株式会社神户制钢所 | Steel material for dissimilar metal joining, joined body of dissimilar metals and process for joining dissimilar metal materials |
| CN103144371A (en) * | 2013-03-26 | 2013-06-12 | 银邦金属复合材料股份有限公司 | Heat-resistant aluminum/steel composite material for brazing |
| US20130280552A1 (en) * | 2010-12-27 | 2013-10-24 | Posco Coated & Color Steel Co., Ltd. | Aluminum Coated Steel Sheet Having Excellent Oxidation Resistance and Heat Resistance |
| 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 |
| CN106367677A (en) * | 2016-08-26 | 2017-02-01 | 银邦金属复合材料股份有限公司 | Steel layer material of brazing composite strip and brazing aluminium-steel composite strip |
| CN107090557A (en) * | 2017-03-13 | 2017-08-25 | 北京工业大学 | A kind of aluminium alloy and preparation method for being used to prepare inexpensive high temperature resistant brazed aluminum/steel composite strip |
| CN111850354A (en) * | 2020-07-29 | 2020-10-30 | 青岛科技大学 | Aluminum alloy and stainless steel composite material and preparation method and application thereof |
-
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- 2021-04-07 CN CN202110373970.6A patent/CN113103688B/en active Active
Patent Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20060275623A1 (en) * | 2005-06-01 | 2006-12-07 | Kabushiki Kaisha Kobe Seiko Sho ( Kobe Steel, Ltd. ) | Steel sheet for dissimilar materials weldbonding to aluminum material and dissimilar materials bonded body |
| CN102066597A (en) * | 2008-06-13 | 2011-05-18 | 株式会社神户制钢所 | Steel material for dissimilar metal joining, joined body of dissimilar metals and process for joining dissimilar metal materials |
| US20130280552A1 (en) * | 2010-12-27 | 2013-10-24 | Posco Coated & Color Steel Co., Ltd. | Aluminum Coated Steel Sheet Having Excellent Oxidation Resistance and Heat Resistance |
| CN103144371A (en) * | 2013-03-26 | 2013-06-12 | 银邦金属复合材料股份有限公司 | Heat-resistant aluminum/steel composite material for brazing |
| 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 |
| CN106367677A (en) * | 2016-08-26 | 2017-02-01 | 银邦金属复合材料股份有限公司 | Steel layer material of brazing composite strip and brazing aluminium-steel composite strip |
| CN107090557A (en) * | 2017-03-13 | 2017-08-25 | 北京工业大学 | A kind of aluminium alloy and preparation method for being used to prepare inexpensive high temperature resistant brazed aluminum/steel composite strip |
| CN111850354A (en) * | 2020-07-29 | 2020-10-30 | 青岛科技大学 | Aluminum alloy and stainless steel composite material and preparation method and application thereof |
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