CN116875864B - Aluminum alloy plate and aluminum alloy composite plate - Google Patents
Aluminum alloy plate and aluminum alloy composite plate Download PDFInfo
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- CN116875864B CN116875864B CN202310763082.4A CN202310763082A CN116875864B CN 116875864 B CN116875864 B CN 116875864B CN 202310763082 A CN202310763082 A CN 202310763082A CN 116875864 B CN116875864 B CN 116875864B
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- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 244
- 239000002131 composite material Substances 0.000 title claims abstract description 135
- 239000010410 layer Substances 0.000 claims abstract description 163
- 230000004888 barrier function Effects 0.000 claims abstract description 147
- 239000012792 core layer Substances 0.000 claims abstract description 95
- 230000032683 aging Effects 0.000 claims abstract description 78
- 238000005219 brazing Methods 0.000 claims abstract description 78
- 238000001816 cooling Methods 0.000 claims abstract description 57
- 239000000463 material Substances 0.000 claims description 67
- 230000007704 transition Effects 0.000 claims description 34
- 238000001556 precipitation Methods 0.000 claims description 26
- 239000012535 impurity Substances 0.000 claims description 17
- 229910052725 zinc Inorganic materials 0.000 claims description 3
- 229910052726 zirconium Inorganic materials 0.000 claims description 3
- 229910052804 chromium Inorganic materials 0.000 claims description 2
- 239000002244 precipitate Substances 0.000 claims description 2
- 230000007797 corrosion Effects 0.000 description 44
- 238000005260 corrosion Methods 0.000 description 44
- 238000005098 hot rolling Methods 0.000 description 40
- 239000000956 alloy Substances 0.000 description 38
- 229910045601 alloy Inorganic materials 0.000 description 36
- 150000001875 compounds Chemical class 0.000 description 34
- 238000003801 milling Methods 0.000 description 31
- 238000005097 cold rolling Methods 0.000 description 30
- 238000005520 cutting process Methods 0.000 description 30
- 238000005728 strengthening Methods 0.000 description 27
- 238000000265 homogenisation Methods 0.000 description 23
- 238000005266 casting Methods 0.000 description 22
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- 239000000203 mixture Substances 0.000 description 17
- 239000011162 core material Substances 0.000 description 12
- 239000006185 dispersion Substances 0.000 description 12
- IUVCFHHAEHNCFT-INIZCTEOSA-N 2-[(1s)-1-[4-amino-3-(3-fluoro-4-propan-2-yloxyphenyl)pyrazolo[3,4-d]pyrimidin-1-yl]ethyl]-6-fluoro-3-(3-fluorophenyl)chromen-4-one Chemical compound C1=C(F)C(OC(C)C)=CC=C1C(C1=C(N)N=CN=C11)=NN1[C@@H](C)C1=C(C=2C=C(F)C=CC=2)C(=O)C2=CC(F)=CC=C2O1 IUVCFHHAEHNCFT-INIZCTEOSA-N 0.000 description 11
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- 239000000243 solution Substances 0.000 description 4
- 238000010998 test method Methods 0.000 description 4
- OKKJLVBELUTLKV-UHFFFAOYSA-N Methanol Chemical compound OC OKKJLVBELUTLKV-UHFFFAOYSA-N 0.000 description 3
- 230000005540 biological transmission Effects 0.000 description 3
- 229910052802 copper Inorganic materials 0.000 description 3
- 238000009826 distribution Methods 0.000 description 3
- 229910052748 manganese Inorganic materials 0.000 description 3
- 238000004519 manufacturing process Methods 0.000 description 3
- 239000002105 nanoparticle Substances 0.000 description 3
- 238000005096 rolling process Methods 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 229910019086 Mg-Cu Inorganic materials 0.000 description 2
- FAPWRFPIFSIZLT-UHFFFAOYSA-M Sodium chloride Chemical compound [Na+].[Cl-] FAPWRFPIFSIZLT-UHFFFAOYSA-M 0.000 description 2
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- 239000002699 waste material Substances 0.000 description 2
- 229910021592 Copper(II) chloride Inorganic materials 0.000 description 1
- 229910021578 Iron(III) chloride Inorganic materials 0.000 description 1
- 229910000861 Mg alloy Inorganic materials 0.000 description 1
- 229910019752 Mg2Si Inorganic materials 0.000 description 1
- 239000007832 Na2SO4 Substances 0.000 description 1
- GRYLNZFGIOXLOG-UHFFFAOYSA-N Nitric acid Chemical compound O[N+]([O-])=O GRYLNZFGIOXLOG-UHFFFAOYSA-N 0.000 description 1
- 238000003723 Smelting Methods 0.000 description 1
- PMZURENOXWZQFD-UHFFFAOYSA-L Sodium Sulfate Chemical compound [Na+].[Na+].[O-]S([O-])(=O)=O PMZURENOXWZQFD-UHFFFAOYSA-L 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
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- 238000006243 chemical reaction Methods 0.000 description 1
- 239000003153 chemical reaction reagent Substances 0.000 description 1
- ORTQZVOHEJQUHG-UHFFFAOYSA-L copper(II) chloride Chemical compound Cl[Cu]Cl ORTQZVOHEJQUHG-UHFFFAOYSA-L 0.000 description 1
- 230000001351 cycling effect Effects 0.000 description 1
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- XLYOFNOQVPJJNP-ZSJDYOACSA-N heavy water Substances [2H]O[2H] XLYOFNOQVPJJNP-ZSJDYOACSA-N 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 230000010354 integration Effects 0.000 description 1
- RBTARNINKXHZNM-UHFFFAOYSA-K iron trichloride Chemical compound Cl[Fe](Cl)Cl RBTARNINKXHZNM-UHFFFAOYSA-K 0.000 description 1
- 239000010985 leather Substances 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 238000007431 microscopic evaluation Methods 0.000 description 1
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Classifications
-
- 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K1/00—Soldering, e.g. brazing, or unsoldering
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- 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
- B32B15/016—Layered products comprising a layer of metal all layers being exclusively metallic all layers being formed of aluminium or aluminium alloys
-
- 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
-
- 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
- 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
- C22C21/18—Alloys based on aluminium with copper as the next major constituent with zinc
-
- 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
-
- 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
-
- 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
- C22F1/057—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 copper as the next major constituent
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B2250/00—Layers arrangement
- B32B2250/03—3 layers
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B2307/00—Properties of the layers or laminate
- B32B2307/50—Properties of the layers or laminate having particular mechanical properties
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B2307/00—Properties of the layers or laminate
- B32B2307/70—Other properties
- B32B2307/714—Inert, i.e. inert to chemical degradation, corrosion
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Conductive Materials (AREA)
Abstract
The invention relates to an aluminum alloy plate and an aluminum alloy composite plate, wherein the aluminum alloy plate contains 0.2-0.7wt% of Si element, 0.95-1.45wt% of Cu element, 0.3-0.9wt% of Mg element, 0.6-1.6wt% of Mn element and more than 0.2wt% of Fe element, the ratio of the content of the Mg element to the content of the Si element is more than or equal to 1.0, and the ratio of the total content of the Fe element and the Mn element to the content of the Si element is more than or equal to 2.0; the aluminum alloy composite board is of a composite layer structure and consists of an upper side barrier layer, a core layer and a lower side barrier layer which are sequentially arranged from top to bottom; the core layer is the aluminum alloy plate. When the temperature cooling rate of the brazing furnace is reduced, the invention can obtain ideal yield strength after natural aging for 1-2 weeks after brazing.
Description
Technical Field
The invention belongs to the technical field of aluminum alloy, and relates to an aluminum alloy plate and an aluminum alloy composite plate.
Background
Aluminum alloy brazing materials are widely used in the manufacture of heat exchanger products such as radiators, condensers, evaporators and the like. With the development of new energy automobiles, energy storage, big data 5G base station and wind power, the heat exchanger is required to be developed in a light weight, the manufacturer also needs to develop the heat exchanger, the brazing material for manufacturing the heat exchanger is required to be updated in a higher strength direction, and the manufacturer needs to develop an aluminum alloy brazing material with high yield strength after 1-2 weeks of natural aging after brazing.
In order to increase the strength of the post-braze alloy, a common approach in the field of brazing is to design a core alloy with age-hardenable properties. For example, high Cu low Mg alloy systems are commonly used, such as those having Cu content of 1.8-2.6wt% and Mg content of 0.6wt% or less, in which Cu, mg are age strengthened alloys that exhibit a higher yield strength after natural aging for 1-2 weeks after brazing, when compared to conventional core alloy AA3003 used to make heat exchangers, when brazed at cooling rates of 200 ℃/min or less.
However, the inventors found through experiments that when the brazing furnace temperature cooling rate is adjusted to a lower level (30 ℃/min), the alloy does not exhibit the ideal yield strength after 1-2 weeks of natural aging after brazing, and the material has a natural aging yield strength of less than 100MPa after brazing for 2 weeks. However, as the field of heat exchangers is gradually developed towards integration and enlargement nowadays, the cooling rate of brazing of practical heat exchangers is generally lower than 30 ℃/min, and a person skilled in the art expects that when the cooling rate of the brazing furnace temperature is reduced, the ideal yield strength after natural aging for 1-2 weeks after brazing can still be obtained.
Disclosure of Invention
The invention aims to solve the problems in the prior art and provides an aluminum alloy plate and an aluminum alloy composite plate.
In order to achieve the above purpose, the invention adopts the following technical scheme:
An aluminum alloy sheet material contains 0.2-0.7wt% of Si element, 0.95-1.45wt% of Cu element, 0.3-0.9wt% of Mg element, 0.6-1.6wt% of Mn element and more than 0.2wt% of Fe element, wherein the ratio of the content of the Mg element to the content of the Si element is more than or equal to 1.0, and the ratio of the total content of the Fe element and the Mn element to the content of the Si element is more than or equal to 2.0.
Experiments show that in an Al-Mg-Cu strengthening system with a small amount or basically no Si, a large amount of micron-sized Al 2Cu/Al2 CuMg phases are separated out at a low cooling rate, but micron-sized Al 2Cu/Al2 CuMg phases are not generated at a high cooling rate; in Al-Mg-Cu strengthening systems containing a large amount of Si element (Si content not less than 0.10 wt%), a large amount of micron-sized Mg 2Si/AlxCu4Mg5Si4 phase is precipitated in addition to micron-sized Al 2Cu/Al2 CuMg phase at a low cooling rate, but only a small amount of micron-sized Mg 2Si/AlxCu4Mg5Si4 phase is precipitated at a high cooling rate. It was found that both the micrometer Al 2Cu/Al2 CuMg phase and the micrometer Mg 2Si/AlxCu4Mg5Si4 phase lead to phenomena that show an ineffective increase in material strength after short-term natural aging after brazing at low cooling rates.
Experiments show that when the Cu content is higher (1.53 wt%), a micrometer Al 2Cu/Al2 CuMg phase is separated out from a matrix in the slow brazing cooling (18-30 ℃/min) process, the supersaturation degree of the alloy is rapidly reduced, the driving force of the subsequent natural aging process is reduced, and enough AlCuMg atomic clusters and a nanometer Al 2 CuMg transition phase are not formed in the subsequent natural aging process to obviously strengthen the alloy; however, as the Cu content was reduced to 1.45wt%, no micron-sized Al 2Cu/Al2 CuMg phase was found to be precipitated at this content under the same slow cooling conditions, which suggests that the reduction of the Cu content to 1.45wt% was able to be substantially all solid-dissolved into the matrix, and it was found that the lower the Cu addition amount was, the higher the supersaturation was relatively, at the same cooling rate.
However, in a high Si system (Si content. Gtoreq.0.10 wt%) even if Cu content is reduced to 1.45wt% or less, there is insufficient strength of the material after short-term natural aging after brazing under the slow cooling condition of brazing as well. The micron-sized Mg 2Si/AlxCu4Mg5Si4 phase was detected under both braze fast and braze slow conditions. When a relatively fast cooling rate (200 ℃/min) is used in the brazing process, although micron-sized Mg 2Si/AlxCu4Mg5Si4 phases are also found to be generated, more AlCuMg atomic clusters and nanoscale Al 2 CuMg transitional phases can be generated due to high supersaturation of Cu element, and the strength of the brazing process after short-term natural aging is not poor, so that the damage to the generation of micron-sized Mg 2Si/AlxCu4Mg5Si4 phases in the brazing slow cooling process is not considered by a person skilled in the art for a long time, but the performance is considered to be reduced due to precipitation of the micron-sized Al 2 CuMg phases. By characterization of finer phase number densities, we found that the micron-sized Mg 2Si/AlxCu4Mg5Si4 phase number density formed under braze slow-cool conditions was much higher than the micron-sized Mg 2Si/AlxCu4Mg5Si4 phase number density formed under braze fast-cool conditions.
When green alloys are prepared in view of scrap recovery, it is inevitable that the system contains at least 0.2wt% of Si impurity element, and at this time, micro-sized Mg 2Si/AlxCu4Mg5Si4 phases are easily generated under the brazing slow cooling condition, resulting in a decrease in the strength of the material after short-term natural aging after brazing. In the invention, when designing the alloy, si element in the alloy needs to exist in a micro-grade AlMnFeSi metal compound or nano-grade AlMnFeCuSiCr disperse phase form instead of Mg 2Si/AlxCu4Mg5Si4 phase form, thereby ensuring that the alloy obtains ideal mechanical properties in a natural aging process after brazing. The Si element is an impurity, usually unavoidable for recycling the old material, and generally allows Si content of at least 0.2wt% to be widely applicable to recycling of the recycled material. In the present invention, it is further required to limit Si element to 0.7% or less, within which it is ensured that conversion of Si element into a AlMnFeSi metal compound of micrometer scale or AlMnFeCuSiCr dispersed phase form of nanometer scale can be achieved, and excessive Si element may cause generation of Mg 2Si/AlxCu4Mg5Si4 phase of micrometer scale.
The known Cu element has good solid solution strengthening effect, is favorable for ensuring that the composite plate has excellent mechanical strength after brazing, and has a general addition amount of more than 1.5wt% (under a brazing quick cooling condition, more than 1.5wt% of Cu cannot cause precipitation of a micrometer-sized Al 2Cu/Al2 CuMg phase and more than 1.45wt% of Cu can form more nanometer-sized Al 2 CuMg phase), but the inventor finds that the adjustment of the addition amount of Cu is extremely important under a brazing slow cooling condition, and the addition amount range of more than 1.5wt% of Cu causes performance failure, so that obvious micrometer-sized Al 2Cu/Al2 CuMg phase is precipitated during microscopic analysis. At most 1.45wt% of Cu element can be added, otherwise, micron-sized Al 2Cu/Al2 CuMg phase is promoted to be separated out; at least 0.95 weight percent of Cu element is required to be added, and the alloy can be dissolved in a matrix under the slow cooling condition of brazing, so that enough AlCuMg atomic clusters and nanoscale Al 2 CuMg transition phases are formed by natural aging for one week after the alloy is brazed, and the performance of the alloy material is not lower than 100MPa after the alloy material is brazed under the condition of simulating low cooling rate (18 ℃/min) and natural aging for 1-2 weeks.
The content of Mg element is controlled to be 0.3-0.9wt%, the Mg element has a strong post-braze solid solution strengthening effect, too little Mg element is unfavorable for promoting AlCuMg atomic clusters and the formation of nano Al 2 CuMg transition phase, and too much Mg element can lead to braze failure (the Mg element reacts with the brazing flux to lead the brazing flux to fail).
The well-known Mn can play a role of solid solution strengthening to improve the mechanical strength of the material. However, in the invention, mn and Fe elements are added, and AlMnFeSi crystalline phase and nano-scale AlMnFeCuSiCr disperse phase can be formed with Si in the alloy, so that Si element in the alloy is consumed, and meanwhile, the mechanical properties of the alloy after brazing and aging can be improved through the dispersion strengthening of nano-scale AlMnFeCuSiCr disperse phase. When the content of Mn element is 0.6-1.6wt%, the content of Fe element is more than 0.20wt%, and the ratio of (Fe+Mn)/Si (i.e. the ratio of the total content of Fe element and Mn element to the content of Si element) is more than or equal to 2.0, si element is induced to combine with Mn element and Fe element to form AlMnFeSi crystal phase. When the content of Mn element and Fe element is too low, si in the alloy cannot be completely consumed, the Si can be promoted to form a coarse Mg 2Si/AlxCu4Mg5Si4 phase, when the content of Mn element is higher than 1.6, the excessive Mn element can be combined with Cu element to form a coarse AlMnCu compound, so that the rolling of the alloy is not facilitated, and the performance after the later natural aging is also not facilitated.
On the other hand, in order to ensure that no micron-sized Mg 2Si/AlxCu4Mg5Si4 phase is formed basically after brazing and aging, namely, the number density of precipitated micron-sized Mg 2Si/AlxCu4Mg5Si4 phases is lower than 100 pieces/mm 2, the Mg/Si is controlled to be more than or equal to 1.0, so that Si in the system is consumed by Fe and Mn as much as possible, and even if a small amount of micron-sized Mg 2Si/AlxCu4Mg5Si4 phases are precipitated in the slow cooling process, enough Mg participates in the later natural aging strengthening process.
As a preferable technical scheme:
an aluminum alloy sheet as described above, the content of Fe element being not more than 0.6wt%; when the Fe content exceeds 0.6wt%, rolling problems may be caused.
An aluminum alloy sheet as described above, further comprising 0.02 to 0.3wt% of Cr element; when Cr element is added into the alloy, the alloy participates in the process of consuming Si element by Fe and Mn element to form a nano AlMnFeCuSiCr disperse phase, and the disperse phase is favorable for improving the comprehensive corrosion resistance.
An aluminum alloy sheet as described above, further comprising 0.02 to 0.2wt% of Ti element and/or 0.05 to 0.2wt% of Zr element; the functions of Ti element and Zr element are well known, zr can be added into the alloy as appropriate, the mechanical property of the alloy is further improved through dispersion strengthening, meanwhile, al 3 Zr phase has the function of inhibiting the growth of recrystallized grains, so that the uniformity of the grain structure of the aluminum alloy after brazing is improved, coarse crystals are avoided, and the formability of the alloy is improved; in the system, alZrCu nanometer level disperse phase is found, so that the mechanical property of the alloy can be further improved; ti is added into the alloy to refine casting grains, so that the grain structure of the alloy is uniform, and the performance stability of the alloy is good.
An aluminum alloy sheet as set forth above, further containing up to 1.0 wt.% Zn element; the addition of Zn element can improve the waste material addition ratio of the material, because many alloys in the heat transmission field contain Zn element, the Zn element can be dissolved in the matrix after brazing, and plays a certain role in strengthening the base material, and meanwhile, the potential of the core material can be conveniently adjusted, but when the Zn addition amount is higher than 1.0wt%, the potential difference between the base material and AlCuMg or nano Al 2 CuMg transition phase is increased, especially the AlCuMg precipitation phase on the grain boundary is caused, so that the inter-crystal corrosion performance is enhanced.
After the aluminum alloy plate is brazed at the cooling rate of 18-30 ℃/min, the main strengthening precipitated phases after natural aging for 1-2 weeks are AlCuMg atomic clusters and nano Al 2 CuMg transitional phases, the micro-scale Al 2Cu/Al2 CuMg phases are not available, and the number density of micro-scale Mg 2Si/AlxCu4Mg5Si4 precipitated phases is lower than 100/mm 2.
The aluminum alloy plate is applied to the field of slow-cooling brazing, wherein the slow-cooling brazing is carried out at a cooling speed of 18-30 ℃/min.
The invention also provides an aluminum alloy composite board, which has a composite layer structure and consists of an upper side barrier layer, a core layer and a lower side barrier layer which are sequentially arranged from top to bottom; the core layer is an aluminum alloy plate as described above; the thickness of the upper side barrier layer or the lower side barrier layer is 7.5-12.5% of the total thickness of the aluminum alloy composite board. The barrier layer is usually used for brazing, prevents the Mg element in the core material from diffusing to the surface, and the control of the thickness is adapted to the addition amount of the Mg element, which is a conventional technical means.
As a preferable technical scheme:
After brazing is carried out on the aluminum alloy composite plate at the cooling rate of 18-30 ℃/min, the main reinforced precipitated phases of the core layer after natural aging for 1-2 weeks are AlCuMg atomic clusters and nano Al 2 CuMg transitional phases, the micro-scale Al 2Cu/Al2 CuMg phases are not contained, and the number density of the micro-scale Mg 2Si/AlxCu4Mg5Si4 phase precipitated phases is lower than 100/mm 2.
According to the aluminum alloy composite plate, the contents of Zn elements in the upper barrier layer and the lower barrier layer are as follows: the potential difference between the upper barrier layer and the core layer is 40-150mv, and the potential difference between the lower barrier layer and the core layer is 40-150mv; reasonable potential difference control is beneficial to intergranular corrosion resistance and comprehensive corrosion resistance of the alloy, and when the core material contains Zn element, the Zn content in the barrier layer needs to be matched timely so as to realize reasonable potential difference.
An aluminum alloy composite panel as described above has a thickness of 0.6 to 2.0mm, and may be, for example, 0.6mm, 1.0mm, 1.2mm, 1.5mm, 1.8mm, 2.0mm, or the like.
The aluminum alloy composite plate is applied to the processing field of slow cold brazing, wherein the slow cold brazing is characterized in that the cooling speed is 18-30 ℃/min.
The beneficial effects are that:
(1) The aluminum alloy plate produced by the invention has excellent mechanical strength, can be directly used for brazing or used as an intermediate material (core material) for preparing a brazing composite plate, and the yield strength of the prepared brazing composite plate after simulated brazing and natural aging for two weeks is more than or equal to 100MPa, and the elongation is more than or equal to 15%.
(2) The aluminum alloy plate and the aluminum alloy composite plate provided by the invention are insensitive to the cooling rate after brazing, and even if the whole brazing cooling rate is lower than 18 ℃/min, the better performance requirements can be met.
(3) The core alloy of the aluminum alloy plate and the aluminum alloy composite plate provided by the invention is allowed to contain 0.2-0.7wt% of Si element, so that not less than 30% of waste can be added, and the requirements of green aluminum production are met.
(4) The aluminum alloy composite board provided by the invention has excellent corrosion resistance, and can ensure that salt spray corrosion (SWAAT) test is not penetrated for 40 days; OY corrosion did not penetrate for 30 days.
Drawings
FIG. 1 is a distribution of nano-sized AlMnFeCuSiCr dispersed phases in a core alloy after brazing of the aluminum alloy composite sheet of example B3;
FIG. 2 is a AlZrCu nm-scale dispersed phase in the core layer after brazing the aluminum alloy composite sheet of example B4;
FIG. 3 is a graph showing the transition phase of nano Al 2 CuMg in the core alloy after two weeks of natural aging after brazing the aluminum alloy composite sheet of example B5.
Detailed Description
The application is further described below in conjunction with the detailed description. It is to be understood that these examples are illustrative of the present application and are not intended to limit the scope of the present application. Furthermore, it should be understood that various changes and modifications can be made by one skilled in the art after reading the teachings of the present application, and such equivalents are intended to fall within the scope of the application as defined in the appended claims.
The term "yield strength" refers to the specified plastic elongation strength (rp 0.2) defined in the GB/T228.1-2010 test method, the industry habit being referred to as yield strength.
The term "elongation" refers to the elongation after break (A) as defined in GB/T228.1-2010 test method, the industry habit being referred to as elongation.
The invention focuses on the adjustment of alloy formula and the slow cooling speed matching of brazing to control after brazing or after 2 weeks aging, the main strengthening precipitated phases of the core layer are AlCuMg atomic clusters and nano Al 2 CuMg transition phases, no micron Al 2Cu/Al2 CuMg phase exists, the number density of precipitated micron Mg 2Si/AlxCu4Mg5Si4 phase is lower than 100/mm 2, and the increase of yield strength after 2 weeks aging after brazing is realized through the control of phases in a system. As is well known to those skilled in the art, for a plate material composed of the same formulation, the final result is not affected by adopting different processing modes, because the nano-scale and small amount of micro-scale compound phases in the original system can be dissolved under the high temperature effect of the brazing temperature, re-dissolved into the matrix, and then some nano-scale dispersed phases or micro-scale coarse precipitated phases are precipitated again in the brazing cooling process.
The test methods for some parameters in the following examples and comparative examples are as follows:
Characterization of the precipitated phases: determining the types and the distribution of precipitated phases in core layer alloy in an aluminum alloy plate or an aluminum alloy composite plate after the simulated brazing treatment is naturally aged for 2 weeks, wherein the type and the distribution of the precipitated phases are specifically TECNAI type transmission electron microscope produced by FEI in America, and the operation voltage is 200KV; carrying out double-spray thinning on the transmission sample in electrolyte of 30vol% nitric acid and 70vol% methanol, wherein the temperature of the electrolyte is controlled to be minus 30 ℃; observing the disperse phase and the precipitate phase in the sample, and taking pictures of different samples under the same magnification.
Mechanical properties: according to GB/T228.1-2010 section 1 of tensile test of metallic Material: the method disclosed in room temperature test method is used for carrying out mechanical property test on an aluminum alloy plate subjected to simulated brazing treatment and aging treatment and an aluminum alloy composite plate subjected to simulated brazing treatment and natural aging for 2 weeks, wherein a test instrument is a ZWICK universal material tester, and test indexes are specified plastic elongation strength (Rp 0.2) and elongation after break (A), and a gauge length of 50mm is used for the test.
OY corrosion experiment: the aluminum alloy composite sheet samples subjected to the simulated brazing treatment and natural aging treatment for 2 weeks are placed in aqueous solutions shown in table 1, and the proportioning concentrations of the solutions are shown in table 1:
TABLE 1OY corrosive solution formulation
| Reagent(s) | NaCl | Na2SO4 | CuCl2·2H2O | FeCl3·6H2O |
| Concentration of | 224.4mg/L | 88.8mg/L | 2.65mg/L | 145.32mg/L |
The experimental temperature cycling conditions were: stirring the solution at 88 ℃ for 8 hours at the stirring speed of 0.6-0.9m/s, then standing and maintaining for 16 hours at room temperature, wherein the experimental period is 30 days, and the surface area ratio of the solution to the aluminum alloy composite board sample is not less than 1cm 2: 5mL. The OY experiment was used to evaluate the condition of the material for both endocorrosion and erosion corrosion, which is characterized by the rate of general corrosion (also known as uniform corrosion) of the material.
Salt spray corrosion: the corrosion depth of an aluminum alloy composite plate sample subjected to natural aging for 2 weeks after simulated brazing treatment is measured by a SWAAT corrosion experiment of ASTMG85-19AnnexA standard for 40 days; wherein, the thickness of the aluminum alloy composite board is 1.0mm; salt spray corrosion is used to evaluate the external corrosion conditions of materials, which are characterized by the conditions of intergranular corrosion and pitting corrosion of the materials.
The specific procedures for the simulated brazing treatment and aging treatment in the following examples and comparative examples are: the annealed sheet was cut longitudinally into test specimens of the corresponding test standard dimensions L X W (240 mm X20 mm), incubated in a brazing furnace for 10 minutes with furnace temperature rise to 600℃, cooled at a cooling rate of 18℃/min, and after the sheet temperature was reduced to 250C, the sheet was removed from the atmosphere and cooled to room temperature, the brazing process was completed, and the brazed specimens were kept at room temperature (25C) for 2 weeks (14 days). The lower the cooling rate, the more detrimental is to achieving AlCuMg atomic clusters and nanoscale Al 2 CuMg transition phases, so the examples only exemplify slow cooling rates under extreme conditions.
Example A1
An aluminum alloy sheet composed of 0.2wt% of Si element, 0.47wt% of Fe element, 0.95wt% of Cu element, 0.6wt% of Mn element, 0.3wt% of Mg element, 0.3wt% of Zn element, 0.05wt% of Zr element, 0.05wt% of Ti element, 0.02wt% of Cr element, the balance of Al element and unavoidable impurities;
The ratio of the content of Mg element to the content of Si element was 1.5, and the ratio of the total content of fe element and Mn element to the content of Si element was 5.35.
The preparation steps of the aluminum alloy plate are as follows:
(1) Batching according to the element composition ratio, and casting to obtain an ingot;
(2) Carrying out high-temperature homogenization treatment on the cast ingot, wherein the heating rate is 100 ℃/h, the homogenization temperature is 500 ℃, and the heat preservation time is 5h;
(3) Cutting and milling the ingot to obtain an aluminum alloy ingot intermediate material, hot-rolling (the temperature is 450 ℃) until the thickness is 6mm, and then cold-rolling until the thickness is 2mm to obtain the aluminum alloy plate.
After brazing is carried out on the finally prepared aluminum alloy plate at a cooling rate of 18 ℃/min, after natural aging for 2 weeks, the main strengthening precipitation phases are AlCuMg atomic clusters and a nanoscale Al 2 CuMg transition phase, no AlMnCr coarse compound exists, no micron-sized Al 2Cu/Al2 CuMg phase exists, a nanoscale AlMnFeCuSiCr dispersion phase is generated, the number density of precipitation of a micron-sized Mg 2Si/AlxCu4Mg5Si4 phase is 5/mm 2, the yield strength is 141.2MPa, and the elongation is 17.2%.
Example A2
An aluminum alloy sheet composed of 0.7wt% of Si element, 0.5wt% of Fe element, 0.95wt% of Cu element, 1wt% of Mn element, 0.9wt% of Mg element, 1wt% of Zn element, 0.05wt% of Zr element, 0.2wt% of Ti element, 0.3wt% of Cr element, the balance of Al element and unavoidable impurities;
the ratio of the content of Mg element to the content of Si element was 1.29, and the ratio of the total content of fe element and Mn element to the content of Si element was 2.14.
The preparation steps of the aluminum alloy plate are as follows:
(1) Batching according to the element composition ratio, and casting to obtain an ingot;
(2) Carrying out high-temperature homogenization treatment on the cast ingot, wherein the heating rate is 100 ℃/h, the homogenization temperature is 500 ℃, and the heat preservation time is 5h;
(3) Cutting and milling the ingot to obtain an aluminum alloy ingot intermediate material, hot-rolling (the temperature is 450 ℃) until the thickness is 6mm, and then cold-rolling until the thickness is 2mm to obtain the aluminum alloy plate.
After brazing is carried out on the finally prepared aluminum alloy plate at a cooling rate of 18 ℃/min, after natural aging for 2 weeks, the main strengthening precipitation phases are AlCuMg atomic clusters and nanoscale Al 2 CuMg transition phases, no AlMnCr coarse compound exists, no micron-sized Al 2Cu/Al2 CuMg phase exists, a nanoscale AlMnFeCuSiCr dispersion phase is generated, the number density of precipitation of micron-sized Mg 2Si/AlxCu4Mg5Si4 phases is 98/mm 2, the yield strength is 138.6MPa, and the elongation is 16.7%.
Comparative example A1
An aluminum alloy sheet, substantially identical to embodiment A2, except that: the aluminum alloy plate has an element composition of 0.45wt% of Fe element, 0.9wt% of Mn element, and a ratio of total content of Fe element and Mn element to content of Si element of 1.93.
After brazing is carried out on the finally prepared aluminum alloy plate at a cooling rate of 18 ℃/min, the main strengthening precipitated phases after natural aging for 2 weeks are AlCuMg atomic clusters and a nanoscale Al 2 CuMg transitional phase, no AlMnCr coarse compound exists, no micron-sized Al 2Cu/Al2 CuMg phase exists, a nanoscale AlMnFeCuSiCr dispersed phase is generated, the number density of precipitated micron-sized Mg 2Si/AlxCu4Mg5Si4 phases is 105/mm 2, the yield strength is 110.3MPa, and the elongation is 18.9%.
Compared with the comparative example A1 and the example A2, (Fe+Mn)/Si is too small, the micron-sized Mg 2Si/AlxCu4Mg5Si4 phase exceeds the standard, and the mechanical property is deteriorated.
Example A3
An aluminum alloy sheet composed of 0.25wt% of Si element, 0.48wt% of Fe element, 1.21wt% of Cu element, 0.82wt% of Mn element, 0.47wt% of Mg element, 0.83wt% of Zn element, 0.17wt% of Zr element, 0.14wt% of Ti element, 0.07wt% of Cr element, the balance of Al element and unavoidable impurities;
The ratio of the content of Mg element to the content of Si element was 1.88, and the ratio of the total content of fe element and Mn element to the content of Si element was 5.2.
The preparation steps of the aluminum alloy plate are as follows:
(1) Batching according to the element composition ratio, and casting to obtain an ingot;
(2) Carrying out high-temperature homogenization treatment on the cast ingot, wherein the heating rate is 100 ℃/h, the homogenization temperature is 500 ℃, and the heat preservation time is 5h;
(3) Cutting and milling the ingot to obtain an aluminum alloy ingot intermediate material, hot-rolling (the temperature is 450 ℃) until the thickness is 6mm, and then cold-rolling until the thickness is 2mm to obtain the aluminum alloy plate.
After brazing is carried out on the finally prepared aluminum alloy plate at a cooling rate of 18 ℃/min, after natural aging for 2 weeks, the main strengthening precipitation phases are AlCuMg atomic clusters and a nanoscale Al 2 CuMg transition phase, no AlMnCr coarse compound exists, no micron-sized Al 2Cu/Al2 CuMg phase exists, a nanoscale AlMnFeCuSiCr dispersion phase is generated, the number density of precipitation of a micron-sized Mg 2Si/AlxCu4Mg5Si4 phase is 12/mm 2, the yield strength is 151.2MPa, and the elongation is 22.3%.
Example A4
An aluminum alloy sheet composed of 0.53wt% of Si element, 0.6wt% of Fe element, 1.19wt% of Cu element, 0.75wt% of Mn element, 0.54wt% of Mg element, 0.9wt% of Zn element, 0.19wt% of Zr element, 0.13wt% of Ti element, 0.05wt% of Cr element, the balance of Al element and unavoidable impurities;
The ratio of the content of Mg element to the content of Si element was 1.02, and the ratio of the total content of fe element and Mn element to the content of Si element was 2.55.
The preparation steps of the aluminum alloy plate are as follows:
(1) Batching according to the element composition ratio, and casting to obtain an ingot;
(2) Carrying out high-temperature homogenization treatment on the cast ingot, wherein the heating rate is 100 ℃/h, the homogenization temperature is 500 ℃, and the heat preservation time is 5h;
(3) Cutting and milling the ingot to obtain an aluminum alloy ingot intermediate material, hot-rolling (the temperature is 450 ℃) until the thickness is 6mm, and then cold-rolling until the thickness is 2mm to obtain the aluminum alloy plate.
After brazing is carried out on the finally prepared aluminum alloy plate at a cooling rate of 18 ℃/min, the main strengthening precipitated phases after natural aging for 2 weeks are AlCuMg atomic clusters and a nanoscale Al 2 CuMg transitional phase, no AlMnCr coarse compound exists, no micron-sized Al 2Cu/Al2 CuMg phase exists, a nanoscale AlMnFeCuSiCr dispersed phase is generated, the number density of precipitated micron-sized Mg 2Si/AlxCu4Mg5Si4 phases is 43/mm 2, the yield strength is 143.3MPa, and the elongation is 18.1%.
Comparative example A2
An aluminum alloy sheet, substantially identical to embodiment A4, except that: the aluminum alloy plate has an element composition of 0.5wt% of Mg element and a ratio of the content of Mg element to the content of Si element of 0.94.
After brazing is carried out on the finally prepared aluminum alloy plate at a cooling rate of 18 ℃/min, after natural aging for 2 weeks, the main strengthening precipitation phases are AlCuMg atomic clusters and nanoscale Al 2 CuMg transition phases, no AlMnCr coarse compound exists, no micron-sized Al 2Cu/Al2 CuMg phase exists, a nanoscale AlMnFeCuSiCr dispersion phase is generated, the number density of precipitation of a micron-sized Mg 2Si/AlxCu4Mg5Si4 phase is 213/mm 2, the yield strength is 106.3MPa, and the elongation is 17.6%.
Compared with the embodiment A4, the comparative example A2 has the Mg/Si of less than 1.0, the micron-sized Mg 2Si/AlxCu4Mg5Si4 phase number density exceeds the standard, and the mechanical property is deteriorated.
Example A5
An aluminum alloy sheet composed of 0.34wt% of Si element, 0.56wt% of Fe element, 1.16wt% of Cu element, 0.74wt% of Mn element, 0.62wt% of Mg element, 0.89wt% of Zn element, 0.2wt% of Zr element, 0.13wt% of Ti element, 0.05wt% of Cr element, the balance of Al element and unavoidable impurities;
The ratio of the content of Mg element to the content of Si element was 1.82, and the ratio of the total content of fe element and Mn element to the content of Si element was 3.82.
The preparation steps of the aluminum alloy plate are as follows:
(1) Batching according to the element composition ratio, and casting to obtain an ingot;
(2) Carrying out high-temperature homogenization treatment on the cast ingot, wherein the heating rate is 100 ℃/h, the homogenization temperature is 500 ℃, and the heat preservation time is 5h;
(3) Cutting and milling the ingot to obtain an aluminum alloy ingot intermediate material, hot-rolling (the temperature is 450 ℃) until the thickness is 6mm, and then cold-rolling until the thickness is 2mm to obtain the aluminum alloy plate.
After brazing is carried out on the finally prepared aluminum alloy plate at a cooling rate of 18 ℃/min, the main strengthening precipitated phases after natural aging for 2 weeks are AlCuMg atomic clusters and nanoscale Al 2 CuMg transitional phases, no AlMnCr coarse compound exists, no micron-sized Al 2Cu/Al2 CuMg phase exists, a nanoscale AlMnFeCuSiCr dispersed phase is generated, the number density of precipitated micron-sized Mg 2Si/AlxCu4Mg5Si4 phases is 15/mm 2, the yield strength is 156.25MPa, and the elongation is 21.5%.
Example A6
An aluminum alloy sheet composed of 0.2wt% of Si element, 0.46wt% of Fe element, 1.45wt% of Cu element, 1.6wt% of Mn element, 0.3wt% of Mg element, 0.3wt% of Zn element, 0.2wt% of Zr element, 0.05wt% of Ti element, 0.3wt% of Cr element, the balance of Al element and unavoidable impurities;
The ratio of the content of Mg element to the content of Si element was 1.5, and the ratio of the total content of fe element and Mn element to the content of Si element was 10.3.
The preparation steps of the aluminum alloy plate are as follows:
(1) Batching according to the element composition ratio, and casting to obtain an ingot;
(2) Carrying out high-temperature homogenization treatment on the cast ingot, wherein the heating rate is 100 ℃/h, the homogenization temperature is 500 ℃, and the heat preservation time is 5h;
(3) Cutting and milling the ingot to obtain an aluminum alloy ingot intermediate material, hot-rolling (the temperature is 450 ℃) until the thickness is 6mm, and then cold-rolling until the thickness is 2mm to obtain the aluminum alloy plate.
After brazing is carried out on the finally prepared aluminum alloy plate at a cooling rate of 18 ℃/min, after natural aging for 2 weeks, the main strengthening precipitation phases are AlCuMg atomic clusters and a nanoscale Al 2 CuMg transition phase, no AlMnCr coarse compound exists, no micron-sized Al 2Cu/Al2 CuMg phase exists, a nanoscale AlMnFeCuSiCr dispersion phase is generated, the number density of precipitation of a micron-sized Mg 2Si/AlxCu4Mg5Si4 phase is 5/mm 2, the yield strength is 147.3MPa, and the elongation is 20.3%.
Example A7
An aluminum alloy sheet composed of 0.2wt% of Si element, 0.2wt% of Fe element, 1.45wt% of Cu element, 1.6wt% of Mn element, 0.9wt% of Mg element, 1wt% of Zn element, 0.2wt% of Zr element, 0.2wt% of Ti element, 0.02wt% of Cr element, the balance of Al element and unavoidable impurities;
The ratio of the content of Mg element to the content of Si element was 4.5, and the ratio of the total content of fe element and Mn element to the content of Si element was 9.0.
The preparation steps of the aluminum alloy plate are as follows:
(1) Batching according to the element composition ratio, and casting to obtain an ingot;
(2) Carrying out high-temperature homogenization treatment on the cast ingot, wherein the heating rate is 100 ℃/h, the homogenization temperature is 500 ℃, and the heat preservation time is 5h;
(3) Cutting and milling the ingot to obtain an aluminum alloy ingot intermediate material, hot-rolling (the temperature is 450 ℃) until the thickness is 6mm, and then cold-rolling until the thickness is 2mm to obtain the aluminum alloy plate.
After brazing is carried out on the finally prepared aluminum alloy plate at a cooling rate of 18 ℃/min, after natural aging for 2 weeks, the main strengthening precipitation phases are AlCuMg atomic clusters and nanoscale Al 2 CuMg transition phases, no AlMnCr coarse compound exists, no micron-sized Al 2Cu/Al2 CuMg phase exists, a nanoscale AlMnFeCuSiCr dispersion phase is generated, the number density of precipitation of a micron-sized Mg 2Si/AlxCu4Mg5Si4 phase is 3/mm 2, the yield strength is 164.9MPa, and the elongation is 17.6%.
Comparative example A3
An aluminum alloy sheet, substantially identical to embodiment A7, except that: the Cu element in the element composition of the aluminum alloy plate is 1.5wt%.
After brazing is carried out on the finally prepared aluminum alloy plate at a cooling rate of 18 ℃/min, the main strengthening precipitated phases after natural aging for 2 weeks are AlCuMg atomic clusters and nanoscale Al 2 CuMg transitional phases, no AlMnCr coarse compound exists, a micron-sized Al 2Cu/Al2 CuMg phase exists, a nanoscale AlMnFeCuSiCr dispersed phase is generated, the number density of precipitated micron-sized Mg 2Si/AlxCu4Mg5Si4 phases is 3/mm 2, the yield strength is 105.4MPa, and the elongation is 16.2%.
Comparative example A3 has a large Cu content compared with example A7, and produces a micrometer-sized Al 2Cu/Al2 CuMg phase, resulting in insufficient main strengthening precipitation phase, affecting yield strength.
Example A8
An aluminum alloy sheet composed of 0.2wt% of Si element, 0.47wt% of Fe element, 0.95wt% of Cu element, 0.6wt% of Mn element, 0.3wt% of Mg element, 0.02wt% of Cr element, the balance of Al element and unavoidable impurities;
The ratio of the content of Mg element to the content of Si element was 1.5, and the ratio of the total content of fe element and Mn element to the content of Si element was 5.35.
The preparation steps of the aluminum alloy plate are as follows:
(1) Batching according to the element composition ratio, and casting to obtain an ingot;
(2) Carrying out high-temperature homogenization treatment on the cast ingot, wherein the heating rate is 100 ℃/h, the homogenization temperature is 500 ℃, and the heat preservation time is 5h;
(3) Cutting and milling the ingot to obtain an aluminum alloy ingot intermediate material, hot-rolling (the temperature is 450 ℃) until the thickness is 6mm, and then cold-rolling until the thickness is 2mm to obtain the aluminum alloy plate.
After brazing is carried out on the finally prepared aluminum alloy plate at a cooling rate of 18 ℃/min, after natural aging for 2 weeks, the main strengthening precipitation phases are AlCuMg atomic clusters and a nanoscale Al 2 CuMg transition phase, no AlMnCr coarse compound exists, no micron-sized Al 2Cu/Al2 CuMg phase exists, a nanoscale AlMnFeCuSiCr dispersion phase is generated, the number density of precipitation of a micron-sized Mg 2Si/AlxCu4Mg5Si4 phase is 5/mm 2, the yield strength is 135.6MPa, and the elongation is 17%.
In comparison between example A8 and example A1, no Ti, zr, zn was added in example A8, alZrCu nm-sized dispersed phase was seen in example A1, and AlZrCu nm-sized dispersed phase was not seen in example A8, and the strength of the aluminum alloy sheet of example A8 was slightly lowered.
Example A9
An aluminum alloy sheet composed of 0.2wt% of Si element, 0.47wt% of Fe element, 0.95wt% of Cu element, 0.6wt% of Mn element, 0.3wt% of Mg element, 1.5wt% of Zn element, 0.05wt% of Zr element, 0.05wt% of Ti element, 0.02wt% of Cr element, the balance of Al element and unavoidable impurities;
The ratio of the content of Mg element to the content of Si element was 1.5, and the ratio of the total content of fe element and Mn element to the content of Si element was 5.35.
The preparation steps of the aluminum alloy plate are as follows:
(1) Batching according to the element composition ratio, and casting to obtain an ingot;
(2) Carrying out high-temperature homogenization treatment on the cast ingot, wherein the heating rate is 100 ℃/h, the homogenization temperature is 500 ℃, and the heat preservation time is 5h;
(3) Cutting and milling the ingot to obtain an aluminum alloy ingot intermediate material, hot-rolling (the temperature is 450 ℃) until the thickness is 6mm, and then cold-rolling until the thickness is 2mm to obtain the aluminum alloy plate.
After brazing is carried out on the finally prepared aluminum alloy plate at a cooling rate of 18 ℃/min, after natural aging for 2 weeks, the main strengthening precipitation phases are AlCuMg atomic clusters and a nanoscale Al 2 CuMg transition phase, no AlMnCr coarse compound exists, no micron-sized Al 2Cu/Al2 CuMg phase exists, a nanoscale AlMnFeCuSiCr dispersion phase is generated, the number density of precipitation of a micron-sized Mg 2Si/AlxCu4Mg5Si4 phase is 5/mm 2, the yield strength is 145.7MPa, and the elongation is 16.9%.
Example A10
An aluminum alloy sheet composed of 0.2wt% of Si element, 0.47wt% of Fe element, 0.95wt% of Cu element, 0.6wt% of Mn element, 0.3wt% of Mg element, 0.3wt% of Zn element, 0.05wt% of Zr element, 0.05wt% of Ti element, the balance of Al element and unavoidable impurities;
The ratio of the content of Mg element to the content of Si element was 1.5, and the ratio of the total content of fe element and Mn element to the content of Si element was 5.35.
The preparation steps of the aluminum alloy plate are as follows:
(1) Batching according to the element composition ratio, and casting to obtain an ingot;
(2) Carrying out high-temperature homogenization treatment on the cast ingot, wherein the heating rate is 100 ℃/h, the homogenization temperature is 500 ℃, and the heat preservation time is 5h;
(3) Cutting and milling the ingot to obtain an aluminum alloy ingot intermediate material, hot-rolling (the temperature is 450 ℃) until the thickness is 6mm, and then cold-rolling until the thickness is 2mm to obtain the aluminum alloy plate.
After brazing is carried out on the finally prepared aluminum alloy plate at a cooling rate of 18 ℃/min, after natural aging for 2 weeks, the main strengthening precipitation phases are AlCuMg atomic clusters and nanoscale Al 2 CuMg transition phases, no AlMnCr coarse compound exists, no micron-sized Al 2Cu/Al2 CuMg phase exists, a nanoscale AlMnFeCuSiCr dispersion phase is generated, the number density of precipitation of micron-sized Mg 2Si/AlxCu4Mg5Si4 phases is 8/mm 2, the yield strength is 133.9MPa, and the elongation is 18.1%.
Example A11
An aluminum alloy sheet composed of 0.2wt% of Si element, 0.47wt% of Fe element, 0.95wt% of Cu element, 0.6wt% of Mn element, 0.3wt% of Mg element, 0.3wt% of Zn element, 0.05wt% of Zr element, 0.05wt% of Ti element, 0.35wt% of Cr element, the balance of Al element and unavoidable impurities;
The ratio of the content of Mg element to the content of Si element was 1.5, and the ratio of the total content of fe element and Mn element to the content of Si element was 5.35.
The preparation steps of the aluminum alloy plate are as follows:
(1) Batching according to the element composition ratio, and casting to obtain an ingot;
(2) Carrying out high-temperature homogenization treatment on the cast ingot, wherein the heating rate is 100 ℃/h, the homogenization temperature is 500 ℃, and the heat preservation time is 5h;
(3) Cutting and milling the ingot to obtain an aluminum alloy ingot intermediate material, hot-rolling (the temperature is 450 ℃) until the thickness is 6mm, and then cold-rolling until the thickness is 2mm to obtain the aluminum alloy plate.
After brazing is carried out on the finally prepared aluminum alloy plate at a cooling rate of 18 ℃/min, after natural aging for 2 weeks, the main strengthening precipitation phases are AlCuMg atomic clusters and a nanoscale Al 2 CuMg transition phase, alMnCr coarse compounds exist, a micron-sized Al 2Cu/Al2 CuMg phase is not generated, a nanoscale AlMnFeCuSiCr dispersion phase is generated, the number density of precipitation of a micron-sized Mg 2Si/AlxCu4Mg5Si4 phase is 7/mm 2, the yield strength is 133.7MPa, and the elongation is 13.2%.
In comparison between example A11 and example A1, the Cr content of example A11 exceeds the standard, and AlMnCr coarse compounds are generated, so that the nano-scale AlMnFeCuSiCr disperse phase is greatly reduced, and the elongation is obviously reduced.
A preparation method of an aluminum alloy composite plate adopts an aluminum alloy ingot intermediate material prepared in the preparation process of an aluminum alloy plate as a core layer ingot; batching according to the composition of the barrier layer alloy elements, smelting and casting to obtain a barrier layer cast ingot, and cutting and milling the surface, wherein the barrier layer alloy can be subjected to no homogenization annealing to obtain larger crystal grains after brazing; in order to facilitate the explanation, the upper barrier layer and the lower barrier layer adopt the same cast ingots, and the upper barrier layer, the core layer and the lower barrier layer cast ingots are heated to 480 ℃ according to the composite ratio of 10:80:10 and then are respectively subjected to hot rolling treatment, and the cast ingots are rolled to target thicknesses (10 mm, 80mm and 10 mm) to obtain a core layer hot rolled plate, a lower barrier layer hot rolled plate and an upper barrier layer hot rolled plate; milling the surface of the core layer hot rolled plate, the lower barrier layer hot rolled plate and the upper barrier layer hot rolled plate, and compositely hot-rolling until the thickness is 5mm; cooling to room temperature, and rolling on a cold rolling mill to a thickness of 1mm to obtain the aluminum alloy composite plate. The single-layer leather accounts for 7.5-12.5% of the total thickness of the composite board, and in the range, the thickness factor does not find the influence factor forming the corrosion performance change; since the barrier layers on both sides are identical, the corrosion performance is characterized by only randomly characterizing the corrosion condition on one side, and the evaluation on the other side is not repeated.
In the following examples, the barrier aluminum alloy ingots of examples B1, B3, B5, and B7 were composed of 0.6wt% of Si element, 0.5wt% of Fe element, 0.15wt% of Cu element, 1.43wt% of Mn element, 0.05wt% of Mg element, 0.05wt% of Cr element, 0.15wt% of Zn element, 0.05wt% of Ti element, 0.05wt% of Zr element, the balance of Al element and unavoidable impurities;
The barrier aluminum alloy ingots of example B2, example B4, and example B6 were composed of 0.5wt% of Si element, 0.2wt% of Fe element, 0.05wt% of Cu element, 0.55wt% of Mn element, 0.05wt% of Mg element, 0.05wt% of Cr element, 0.05wt% of Zn element, 0.04wt% of Ti element, 0.05wt% of Zr element, the balance of Al element, and unavoidable impurities;
The barrier aluminum alloy ingots of example B12, example B13 consisted of 0.8wt% Si element, 0.5wt% Fe element, 0.15wt% Cu element, 0.1wt% Mn element, 0.05wt% Mg element, 0.05wt% Cr element, 0.5wt% Zn element, 0.05wt% Ti element, 0.05wt% Zr element, the balance Al element and unavoidable impurities.
Example B1
The preparation method of the aluminum alloy composite board comprises the following steps:
(1) Carrying out hot rolling treatment;
the intermediate material of the aluminum alloy ingot casting of the embodiment A1 is hot rolled (the temperature is 480 ℃) to the thickness of 80mm, and a core layer hot rolled plate is obtained;
Hot rolling the two barrier layer aluminum alloy cast ingot intermediate materials (the temperature is 480 ℃) to 10mm in thickness to obtain a lower barrier layer hot rolled plate and an upper barrier layer hot rolled plate;
(2) Cutting and milling the surface;
Cutting and milling surfaces of the core layer hot rolled plate, the lower barrier layer hot rolled plate and the upper barrier layer hot rolled plate respectively;
(3) Compounding;
and (3) sequentially compounding the upper barrier layer hot rolled plate, the core layer hot rolled plate and the lower barrier layer hot rolled plate, hot rolling to a thickness of 5mm, and then cold rolling (adopting a cold rolling mill at room temperature) to a thickness of 1mm to obtain the aluminum alloy composite plate.
The finally prepared aluminum alloy composite board has a composite layer structure and consists of an upper side barrier layer, a core layer and a lower side barrier layer which are sequentially arranged from top to bottom;
After the aluminum alloy composite plate is brazed at a cooling rate of 18 ℃/min, the yield strength after 2 weeks of natural aging is 114.4MPa, the elongation is 17.2%, and the potential difference between the upper barrier layer and the core layer is 45mv;
After 2 weeks of natural aging, the main reinforced precipitated phases of the core layer are AlCuMg atomic clusters and nanoscale Al 2 CuMg transition phases, no AlMnCr coarse compound exists, no micron-sized Al 2Cu/Al2 CuMg phase exists, a nanoscale AlMnFeCuSiCr dispersed phase is generated, and the number density of precipitated micron-sized Mg 2Si/AlxCu4Mg5Si4 phases is 5/mm 2;
the salt spray corrosion depth of the aluminum alloy composite plate is 175 mu m; the OY etch depth was 100. Mu.m.
Example B2
The preparation method of the aluminum alloy composite board comprises the following steps:
(1) Carrying out hot rolling treatment;
the intermediate material of the aluminum alloy ingot casting of the embodiment A2 is hot rolled (the temperature is 480 ℃) to the thickness of 80mm, and a core layer hot rolled plate is obtained;
Hot rolling the two barrier layer aluminum alloy cast ingot intermediate materials (the temperature is 480 ℃) to 10mm in thickness to obtain a lower barrier layer hot rolled plate and an upper barrier layer hot rolled plate;
(2) Cutting and milling the surface;
Cutting and milling surfaces of the core layer hot rolled plate, the lower barrier layer hot rolled plate and the upper barrier layer hot rolled plate respectively;
(3) Compounding;
and (3) sequentially compounding the upper barrier layer hot rolled plate, the core layer hot rolled plate and the lower barrier layer hot rolled plate, hot rolling to a thickness of 5mm, and then cold rolling (adopting a cold rolling mill at room temperature) to a thickness of 1mm to obtain the aluminum alloy composite plate.
The finally prepared aluminum alloy composite board has a composite layer structure and consists of an upper side barrier layer, a core layer and a lower side barrier layer which are sequentially arranged from top to bottom;
after the aluminum alloy composite plate is brazed at a cooling rate of 18 ℃/min, the yield strength after 2 weeks of natural aging is 112.3MPa, the elongation is 16.3%, and the potential difference between the upper barrier layer and the core layer is 70mv;
After 2 weeks of natural aging, the main reinforced precipitated phases of the core layer are AlCuMg atomic clusters and nanoscale Al 2 CuMg transition phases, no AlMnCr coarse compound exists, no micron-sized Al 2Cu/Al2 CuMg phase exists, and the number density of precipitated micron-sized Mg 2Si/AlxCu4Mg5Si4 phases is 98/mm 2;
the salt spray corrosion depth of the aluminum alloy composite board is 295 mu m; the OY etch depth was 139. Mu.m.
Comparative example C1
A method for preparing an aluminum alloy composite panel, which is basically the same as that of example B2, and is different only in that: the aluminum alloy ingot intermediate material of example A2 in step (1) was replaced with the aluminum alloy ingot intermediate material of comparative example A1.
The finally prepared aluminum alloy composite board has a composite layer structure and consists of an upper side barrier layer, a core layer and a lower side barrier layer which are sequentially arranged from top to bottom;
After the aluminum alloy composite plate is brazed at a cooling rate of 18 ℃/min, the yield strength after 2 weeks of natural aging is 89.3MPa, the elongation is 18.9%, and the potential difference between the upper barrier layer and the core layer is 70mv;
After 2 weeks of natural aging, the main reinforced precipitated phases of the core layer are AlCuMg atomic clusters and nanoscale Al 2 CuMg transition phases, no AlMnCr coarse compound exists, no micron-sized Al 2Cu/Al2 CuMg phase exists, a nanoscale AlMnFeCuSiCr dispersed phase is generated, and the number density of precipitated micron-sized Mg 2Si/AlxCu4Mg5Si4 phases is 105/mm 2;
The salt spray corrosion depth of the aluminum alloy composite board is 281 mu m; the OY etch depth was 100. Mu.m.
As can be seen from comparison of comparative example C1 with example B2, (Fe+Mn)/Si is too small, the number density of the micron-sized Mg 2Si/AlxCu4Mg5Si4 phase exceeds the standard, and the mechanical properties are deteriorated.
Example B3
The preparation method of the aluminum alloy composite board comprises the following steps:
(1) Carrying out hot rolling treatment;
the intermediate material of the aluminum alloy ingot casting of the embodiment A3 is hot rolled (the temperature is 480 ℃) to the thickness of 80mm, and a core layer hot rolled plate is obtained;
Hot rolling the two barrier layer aluminum alloy cast ingot intermediate materials (the temperature is 480 ℃) to 10mm in thickness to obtain a lower barrier layer hot rolled plate and an upper barrier layer hot rolled plate;
(2) Cutting and milling the surface;
Cutting and milling surfaces of the core layer hot rolled plate, the lower barrier layer hot rolled plate and the upper barrier layer hot rolled plate respectively;
(3) Compounding;
and (3) sequentially compounding the upper barrier layer hot rolled plate, the core layer hot rolled plate and the lower barrier layer hot rolled plate, hot rolling to a thickness of 5mm, and then cold rolling (adopting a cold rolling mill at room temperature) to a thickness of 1mm to obtain the aluminum alloy composite plate.
The finally prepared aluminum alloy composite board has a composite layer structure and consists of an upper side barrier layer, a core layer and a lower side barrier layer which are sequentially arranged from top to bottom;
after the aluminum alloy composite plate is brazed at a cooling rate of 18 ℃/min, the yield strength after 2 weeks of natural aging is 122.5MPa, the elongation is 22.3%, and the potential difference between the upper barrier layer and the core layer is 50mv;
After 2 weeks of natural aging, the main reinforced precipitated phases of the core layer are AlCuMg atomic clusters and nanoscale Al 2 CuMg transition phases, no AlMnCr coarse compound and no micron-sized Al 2Cu/Al2 CuMg phase are generated, as shown in figure 1, the nano-sized AlMnFeCuSiCr dispersed phases are generated, and the number density of precipitated phases of the micron-sized Mg 2Si/AlxCu4Mg5Si4 is 12/mm 2;
the salt spray corrosion depth of the aluminum alloy composite board is 255 mu m; the OY etch depth was 73 μm.
Example B4
The preparation method of the aluminum alloy composite board comprises the following steps:
(1) Carrying out hot rolling treatment;
The intermediate material of the aluminum alloy ingot casting of the embodiment A4 is hot rolled (the temperature is 480 ℃) to the thickness of 80mm, and a core layer hot rolled plate is obtained;
Hot rolling the two barrier layer aluminum alloy cast ingot intermediate materials (the temperature is 480 ℃) to 10mm in thickness to obtain a lower barrier layer hot rolled plate and an upper barrier layer hot rolled plate;
(2) Cutting and milling the surface;
Cutting and milling surfaces of the core layer hot rolled plate, the lower barrier layer hot rolled plate and the upper barrier layer hot rolled plate respectively;
(3) Compounding;
and (3) sequentially compounding the upper barrier layer hot rolled plate, the core layer hot rolled plate and the lower barrier layer hot rolled plate, hot rolling to a thickness of 5mm, and then cold rolling (adopting a cold rolling mill at room temperature) to a thickness of 1mm to obtain the aluminum alloy composite plate.
The finally prepared aluminum alloy composite board has a composite layer structure and consists of an upper side barrier layer, a core layer and a lower side barrier layer which are sequentially arranged from top to bottom;
After the aluminum alloy composite plate is brazed at a cooling rate of 18 ℃/min, the yield strength after 2 weeks of natural aging is 116.1MPa, the elongation is 18.1%, and the potential difference between the upper barrier layer and the core layer is 80mv;
After 2 weeks of natural aging, the main reinforced precipitated phases of the core layer are AlCuMg atomic clusters and nanoscale Al 2 CuMg transition phases, no AlMnCr coarse compound and no micron-sized Al 2Cu/Al2 CuMg phase are generated, as shown in figure 2, the nano-sized AlMnFeCuSiCr dispersed phases are generated, and the number density of precipitated phases of the micron-sized Mg 2Si/AlxCu4Mg5Si4 is 43/mm 2;
the salt spray corrosion depth of the aluminum alloy composite board is 263 mu m; the OY etch depth was 93 μm.
Comparative example C2
A method for preparing an aluminum alloy composite panel, which is basically the same as in example B4, except that: the aluminum alloy ingot intermediate material of example A4 in step (1) was replaced with the aluminum alloy ingot intermediate material of comparative example A2.
The finally prepared aluminum alloy composite board has a composite layer structure and consists of an upper side barrier layer, a core layer and a lower side barrier layer which are sequentially arranged from top to bottom;
after the aluminum alloy composite plate is brazed at a cooling rate of 18 ℃/min, the yield strength after 2 weeks of natural aging is 86.1MPa, the elongation is 17.1%, and the potential difference between the upper barrier layer and the core layer is 80mv;
After 2 weeks of natural aging, the main reinforced precipitated phases of the core layer are AlCuMg atomic clusters and nanoscale Al 2 CuMg transition phases, no AlMnCr coarse compound exists, no micron-sized Al 2Cu/Al2 CuMg phase exists, a nanoscale AlMnFeCuSiCr dispersed phase is generated, and the number density of precipitated micron-sized Mg 2Si/AlxCu4Mg5Si4 phases is 150/mm 2;
The salt spray corrosion depth of the aluminum alloy composite board is 273 mu m; the OY etch depth was 96. Mu.m.
Comparing comparative example C2 with example B4, it can be seen that the Mg/Si is less than 1.0, the micron-sized Mg2Si/AlxCu Mg5Si4 phase number density exceeds the standard, and the mechanical property is deteriorated.
Example B5
The preparation method of the aluminum alloy composite board comprises the following steps:
(1) Carrying out hot rolling treatment;
the intermediate material of the aluminum alloy ingot casting of the embodiment A5 is hot rolled (the temperature is 480 ℃) to the thickness of 80mm, and a core layer hot rolled plate is obtained;
Hot rolling the two barrier layer aluminum alloy cast ingot intermediate materials (the temperature is 480 ℃) to 10mm in thickness to obtain a lower barrier layer hot rolled plate and an upper barrier layer hot rolled plate;
(2) Cutting and milling the surface;
Cutting and milling surfaces of the core layer hot rolled plate, the lower barrier layer hot rolled plate and the upper barrier layer hot rolled plate respectively;
(3) Compounding;
and (3) sequentially compounding the upper barrier layer hot rolled plate, the core layer hot rolled plate and the lower barrier layer hot rolled plate, hot rolling to a thickness of 5mm, and then cold rolling (adopting a cold rolling mill at room temperature) to a thickness of 1mm to obtain the aluminum alloy composite plate.
The finally prepared aluminum alloy composite board has a composite layer structure and consists of an upper side barrier layer, a core layer and a lower side barrier layer which are sequentially arranged from top to bottom;
after the aluminum alloy composite plate is brazed at a cooling rate of 18 ℃/min, the yield strength after 2 weeks of natural aging is 126.6MPa, the elongation is 21.5%, and the potential difference between the upper barrier layer and the core layer is 60mv;
As shown in fig. 3, after 2 weeks of natural aging, the main reinforced precipitated phases of the core layer are AlCuMg atomic clusters and nano-scale Al 2 CuMg transition phases, no AlMnCr coarse compound exists, no micro-scale Al 2Cu/Al2 CuMg phase exists, nano-scale AlMnFeCuSiCr dispersed phases are generated, and the number density of precipitated micro-scale Mg 2Si/AlxCu4Mg5Si4 phases is 15/mm 2;
the salt spray corrosion depth of the aluminum alloy composite plate is 237 mu m; the OY etch depth was 90. Mu.m.
Example B6
The preparation method of the aluminum alloy composite board comprises the following steps:
(1) Carrying out hot rolling treatment;
the intermediate material of the aluminum alloy ingot casting of the embodiment A6 is hot rolled (the temperature is 480 ℃) to the thickness of 80mm, and a core layer hot rolled plate is obtained;
Hot rolling the two barrier layer aluminum alloy cast ingot intermediate materials (the temperature is 480 ℃) to 10mm in thickness to obtain a lower barrier layer hot rolled plate and an upper barrier layer hot rolled plate;
(2) Cutting and milling the surface;
Cutting and milling surfaces of the core layer hot rolled plate, the lower barrier layer hot rolled plate and the upper barrier layer hot rolled plate respectively;
(3) Compounding;
and (3) sequentially compounding the upper barrier layer hot rolled plate, the core layer hot rolled plate and the lower barrier layer hot rolled plate, hot rolling to a thickness of 5mm, and then cold rolling (adopting a cold rolling mill at room temperature) to a thickness of 1mm to obtain the aluminum alloy composite plate.
The finally prepared aluminum alloy composite board has a composite layer structure and consists of an upper side barrier layer, a core layer and a lower side barrier layer which are sequentially arranged from top to bottom;
After the aluminum alloy composite plate is brazed at a cooling rate of 18 ℃/min, the yield strength after 2 weeks of natural aging is 119.3MPa, the elongation is 20.3%, and the potential difference between the upper barrier layer and the core layer is 120mv;
After 2 weeks of natural aging, the main reinforced precipitated phases of the core layer are AlCuMg atomic clusters and nanoscale Al 2 CuMg transition phases, no AlMnCr coarse compound exists, no micron-sized Al 2Cu/Al2 CuMg phase exists, a nanoscale AlMnFeCuSiCr dispersed phase is generated, and the number density of precipitated micron-sized Mg 2Si/AlxCu4Mg5Si4 phases is 5/mm 2;
the salt spray corrosion depth of the aluminum alloy composite board is 213 mu m; the OY etch depth was 150. Mu.m.
Example B7
The preparation method of the aluminum alloy composite board comprises the following steps:
(1) Carrying out hot rolling treatment;
the intermediate material of the aluminum alloy ingot casting of the embodiment A7 is hot rolled (the temperature is 480 ℃) to the thickness of 80mm, and a core layer hot rolled plate is obtained;
Hot rolling the two barrier layer aluminum alloy cast ingot intermediate materials (the temperature is 480 ℃) to 10mm in thickness to obtain a lower barrier layer hot rolled plate and an upper barrier layer hot rolled plate;
(2) Cutting and milling the surface;
Cutting and milling surfaces of the core layer hot rolled plate, the lower barrier layer hot rolled plate and the upper barrier layer hot rolled plate respectively;
(3) Compounding;
and (3) sequentially compounding the upper barrier layer hot rolled plate, the core layer hot rolled plate and the lower barrier layer hot rolled plate, hot rolling to a thickness of 5mm, and then cold rolling (adopting a cold rolling mill at room temperature) to a thickness of 1mm to obtain the aluminum alloy composite plate.
The finally prepared aluminum alloy composite board has a composite layer structure and consists of an upper side barrier layer, a core layer and a lower side barrier layer which are sequentially arranged from top to bottom;
After the aluminum alloy composite plate is brazed at a cooling rate of 18 ℃/min, the yield strength after 2 weeks of natural aging is 133.6MPa, the elongation is 17.6%, and the potential difference between the upper barrier layer and the core layer is 100mv;
After 2 weeks of natural aging, the main reinforced precipitated phases of the core layer are AlCuMg atomic clusters and nanoscale Al 2 CuMg transition phases, no AlMnCr coarse compound exists, no micron-sized Al 2Cu/Al2 CuMg phase exists, a nanoscale AlMnFeCuSiCr dispersed phase is generated, and the number density of precipitated micron-sized Mg 2Si/AlxCu4Mg5Si4 phases is 3/mm 2;
The salt spray corrosion depth of the aluminum alloy composite board is 333 mu m; the OY etch depth was 105. Mu.m.
Comparative example C3
A method for preparing an aluminum alloy composite panel, which is basically the same as in example B7, except that: the aluminum alloy ingot intermediate material of example A7 in step (1) was replaced with the aluminum alloy ingot intermediate material of comparative example A3.
The finally prepared aluminum alloy composite board has a composite layer structure and consists of an upper side barrier layer, a core layer and a lower side barrier layer which are sequentially arranged from top to bottom;
after the aluminum alloy composite plate is brazed at a cooling rate of 18 ℃/min, the yield strength after 2 weeks of natural aging is 85.4MPa, the elongation is 15.2%, and the potential difference between the upper barrier layer and the core layer is 110mv;
After 2 weeks of natural aging, the main reinforced precipitated phases of the core layer are AlCuMg atomic clusters and nanoscale Al 2 CuMg transition phases, no AlMnCr coarse compound exists, a micron-sized Al 2Cu/Al2 CuMg phase exists, a nanoscale AlMnFeCuSiCr dispersed phase is generated, and the number density of precipitated micron-sized Mg 2Si/AlxCu4Mg5Si4 phases is 10/mm 2;
The salt spray corrosion depth of the aluminum alloy composite board is 294 mu m; the OY etch depth was 182 μm.
Comparing comparative example C3 with example B7 shows that the Cu content is large, and a micrometer-sized Al 2Cu/Al2 CuMg phase is generated, so that the main strengthening precipitation phase is insufficient, and the yield strength is affected.
Example B8
A method for preparing an aluminum alloy composite panel, which is basically the same as that of example B1, and is different only in that: the aluminum alloy ingot intermediate material of example A1 in step (1) was replaced with the aluminum alloy ingot intermediate material of example A8.
The finally prepared aluminum alloy composite board has a composite layer structure and consists of an upper side barrier layer, a core layer and a lower side barrier layer which are sequentially arranged from top to bottom;
After the aluminum alloy composite plate is brazed at a cooling rate of 18 ℃/min, the yield strength after 2 weeks of natural aging is 109.8MPa, the elongation is 17%, and the potential difference between the upper barrier layer and the core layer is 63mv;
After 2 weeks of natural aging, the main reinforced precipitated phases of the core layer are AlCuMg atomic clusters and nanoscale Al 2 CuMg transition phases, no AlMnCr coarse compound exists, no micron-sized Al 2Cu/Al2 CuMg phase exists, a nanoscale AlMnFeCuSiCr dispersed phase is generated, and the number density of precipitated micron-sized Mg 2Si/AlxCu4Mg5Si4 phases is 5/mm 2;
the salt spray corrosion depth of the aluminum alloy composite board is 155 mu m; the OY etch depth was 98. Mu.m.
As can be seen by comparing example B1 with example B8, without the addition of Ti or Zr, alZrCu nm-sized dispersed phase was seen in example B1, while AlZrCu nm-sized dispersed phase was not seen in example B8, and the strength of the aluminum alloy composite panel of example B8 was slightly lowered.
Example B9
A method for preparing an aluminum alloy composite panel, which is basically the same as that of example B1, and is different only in that: the aluminum alloy ingot intermediate material of example A1 in step (1) was replaced with the aluminum alloy ingot intermediate material of example A9.
The finally prepared aluminum alloy composite board has a composite layer structure and consists of an upper side barrier layer, a core layer and a lower side barrier layer which are sequentially arranged from top to bottom;
After the aluminum alloy composite plate is brazed at a cooling rate of 18 ℃/min, the yield strength after 2 weeks of natural aging is 118MPa, the elongation is 16.9%, and the potential difference between the upper barrier layer and the core layer is 40mv;
After 2 weeks of natural aging, the main reinforced precipitated phases of the core layer are AlCuMg atomic clusters and nanoscale Al 2 CuMg transition phases, no AlMnCr coarse compound exists, no micron-sized Al 2Cu/Al2 CuMg phase exists, a nanoscale AlMnFeCuSiCr dispersed phase is generated, and the number density of precipitated micron-sized Mg 2Si/AlxCu4Mg5Si4 phases is 5/mm 2;
The salt spray corrosion depth of the aluminum alloy composite plate penetrates through the aluminum alloy composite plate; the OY etch depth was 137. Mu.m.
As can be seen by comparing example B1 with example B9, too much Zn element was added to the core material of example B9, resulting in penetration of the salt spray corrosion sample and a decrease in intergranular corrosion resistance.
Example B10
A method for preparing an aluminum alloy composite panel, which is basically the same as that of example B1, and is different only in that: the aluminum alloy ingot intermediate material of example A1 in step (1) was replaced with the aluminum alloy ingot intermediate material of example a 10.
The finally prepared aluminum alloy composite board has a composite layer structure and consists of an upper side barrier layer, a core layer and a lower side barrier layer which are sequentially arranged from top to bottom;
After the aluminum alloy composite plate is brazed at a cooling rate of 18 ℃/min, the yield strength after 2 weeks of natural aging is 108.5MPa, the elongation is 18.1%, and the potential difference between the upper barrier layer and the core layer is 50mv;
After 2 weeks of natural aging, the main reinforced precipitated phases of the core layer are AlCuMg atomic clusters and nanoscale Al 2 CuMg transition phases, no AlMnCr coarse compound exists, no micron-sized Al 2Cu/Al2 CuMg phase exists, a nanoscale AlMnFeCuSiCr dispersed phase is generated, and the number density of precipitated micron-sized Mg 2Si/AlxCu4Mg5Si4 phases is 8/mm 2;
The salt spray corrosion depth of the aluminum alloy composite board is 183 mu m; the OY etch depth has penetrated the aluminum alloy composite panel.
As can be seen by comparing example B1 with example B10, the core material of example B10 was free of Cr, and had poor corrosion resistance and a large OY depth.
Example B11
A method for preparing an aluminum alloy composite panel, which is basically the same as that of example B1, and is different only in that: the aluminum alloy ingot intermediate material of example A1 in step (1) was replaced with the aluminum alloy ingot intermediate material of example a 11.
The finally prepared aluminum alloy composite board has a composite layer structure and consists of an upper side barrier layer, a core layer and a lower side barrier layer which are sequentially arranged from top to bottom;
After the aluminum alloy composite plate is brazed at a cooling rate of 18 ℃/min, the yield strength after 2 weeks of natural aging is 108.3MPa, the elongation is 13%, and the potential difference between the upper barrier layer and the core layer is 45mv;
After 2 weeks of natural aging, the main reinforced precipitated phases of the core layer are AlCuMg atomic clusters and nanoscale Al 2 CuMg transition phases, alMnCr coarse compounds exist, a micron-sized Al 2Cu/Al2 CuMg phase is not generated, a nanoscale AlMnFeCuSiCr dispersed phase is generated, and the number density of precipitated micron-sized Mg 2Si/AlxCu4Mg5Si4 phases is 7/mm 2;
the salt spray corrosion depth of the aluminum alloy composite plate penetrates through the aluminum alloy composite plate; the OY corrosion depth is the pitting corrosion penetrating through the aluminum alloy composite panel.
As can be seen by comparing example B1 with example B11, the Cr content in the core material of example B11 exceeds the standard, and AlMnCr coarse compounds are generated, so that the nano-scale AlMnFeCuSiCr dispersed phase is greatly reduced, the elongation is obviously reduced, and the OY and salt spray corrosion resistance is reduced.
Example B12
The preparation method of the aluminum alloy composite board comprises the following steps:
(1) Carrying out hot rolling treatment;
The intermediate material of the aluminum alloy ingot casting of the embodiment A4 is hot rolled (the temperature is 480 ℃) to the thickness of 80mm, and a core layer hot rolled plate is obtained;
Hot rolling the two barrier layer aluminum alloy cast ingot intermediate materials (the temperature is 480 ℃) to 10mm in thickness to obtain a lower barrier layer hot rolled plate and an upper barrier layer hot rolled plate;
(2) Cutting and milling the surface;
Cutting and milling surfaces of the core layer hot rolled plate, the lower barrier layer hot rolled plate and the upper barrier layer hot rolled plate respectively;
(3) Compounding;
and (3) sequentially compounding the upper barrier layer hot rolled plate, the core layer hot rolled plate and the lower barrier layer hot rolled plate, hot rolling to a thickness of 5mm, and then cold rolling (adopting a cold rolling mill at room temperature) to a thickness of 1mm to obtain the aluminum alloy composite plate.
The finally prepared aluminum alloy composite board has a composite layer structure and consists of an upper side barrier layer, a core layer and a lower side barrier layer which are sequentially arranged from top to bottom;
after the aluminum alloy composite plate is brazed at a cooling rate of 18 ℃/min, the yield strength after 2 weeks of natural aging is 111.8MPa, the elongation is 17.6%, and the potential difference between the upper barrier layer and the core layer is 143mv;
After 2 weeks of natural aging, the main reinforced precipitated phases of the core layer are AlCuMg atomic clusters and nanoscale Al 2 CuMg transition phases, no AlMnCr coarse compound exists, no micron-sized Al 2Cu/Al2 CuMg phase exists, a nanoscale AlMnFeCuSiCr dispersed phase is generated, and the number density of precipitated micron-sized Mg 2Si/AlxCu4Mg5Si4 phases is 40/mm 2;
The salt spray corrosion depth of the aluminum alloy composite board is 650 mu m; the OY etch depth was 360 μm.
Example B13
The preparation method of the aluminum alloy composite board comprises the following steps:
(1) Carrying out hot rolling treatment;
The intermediate material of the aluminum alloy ingot casting of the embodiment A8 is hot rolled (the temperature is 480 ℃) to the thickness of 80mm, and a core layer hot rolled plate is obtained;
Hot rolling the two barrier layer aluminum alloy cast ingot intermediate materials (the temperature is 480 ℃) to 10mm in thickness to obtain a lower barrier layer hot rolled plate and an upper barrier layer hot rolled plate;
(2) Cutting and milling the surface;
Cutting and milling surfaces of the core layer hot rolled plate, the lower barrier layer hot rolled plate and the upper barrier layer hot rolled plate respectively;
(3) Compounding;
and (3) sequentially compounding the upper barrier layer hot rolled plate, the core layer hot rolled plate and the lower barrier layer hot rolled plate, hot rolling to a thickness of 5mm, and then cold rolling (adopting a cold rolling mill at room temperature) to a thickness of 1mm to obtain the aluminum alloy composite plate.
The finally prepared aluminum alloy composite board has a composite layer structure and consists of an upper side barrier layer, a core layer and a lower side barrier layer which are sequentially arranged from top to bottom;
After the aluminum alloy composite plate is brazed at a cooling rate of 18 ℃/min, the yield strength after 2 weeks of natural aging is 108.5MPa, the elongation is 17.5%, and the potential difference between the upper barrier layer and the core layer is 160mv;
After 2 weeks of natural aging, the main reinforced precipitated phases of the core layer are AlCuMg atomic clusters and nanoscale Al 2 CuMg transition phases, no AlMnCr coarse compound exists, no micron-sized Al 2Cu/Al2 CuMg phase exists, a nanoscale AlMnFeCuSiCr dispersed phase is generated, and the number density of precipitated micron-sized Mg 2Si/AlxCu4Mg5Si4 phases is 7/mm 2;
The corrosion is accelerated due to the overlarge potential difference between the upper barrier layer and the core layer, so that the salt fog corrosion depth of the aluminum alloy composite plate penetrates through the aluminum alloy composite plate; the OY etch depth was 415 μm.
The detailed structural features of the present invention are described in the above embodiments, but the present invention is not limited to the above detailed structural features, that is, it does not mean that the present invention must be implemented depending on the above detailed structural features. It should be apparent to those skilled in the art that any modifications of the present invention, equivalent substitutions of selected components of the present invention, addition of auxiliary components, selection of specific modes, etc., are within the scope of the present invention and the scope of the disclosure.
Claims (9)
1. An aluminum alloy sheet material characterized by comprising 0.2 to 0.7wt% of Si element, 0.95 to 1.45wt% of Cu element, 0.3 to 0.9wt% of Mg element, 0.6 to 1.6wt% of Mn element, more than 0.2wt% of Fe element, the balance of Al element and unavoidable impurities, wherein the ratio of the content of Mg element to the content of Si element is not less than 1.0, and the ratio of the total content of Fe element and Mn element to the content of Si element is not less than 2.0; after the aluminum alloy plate is brazed at the cooling rate of 18-30 ℃/min, the main reinforced precipitated phases after natural aging for 1-2 weeks are AlCuMg atomic clusters and nano Al 2 CuMg transitional phases, the micro-scale Al 2Cu/Al2 CuMg phases are not available, and the number density of the micro-scale Mg 2Si/AlxCu4Mg5Si4 phase precipitated phases is lower than 100/mm 2.
2. An aluminium alloy sheet according to claim 1, wherein the content of Fe element is not more than 0.6wt%.
3. An aluminium alloy sheet according to claim 1, further comprising 0.02-0.3wt% Cr element.
4. An aluminium alloy sheet according to claim 1, further comprising 0.02-0.2wt% Ti element and/or 0.05-0.2wt% Zr element.
5. An aluminium alloy sheet according to claim 1, further comprising at most 1.0wt% Zn element.
6. The aluminum alloy composite board is characterized by having a composite layer structure, and comprising an upper side barrier layer, a core layer and a lower side barrier layer which are sequentially arranged from top to bottom; the core layer is an aluminum alloy plate material as set forth in any one of claims 1 to 5; the thickness of the upper side barrier layer or the lower side barrier layer is 7.5-12.5% of the total thickness of the aluminum alloy composite board.
7. An aluminum alloy composite panel as claimed in claim 6, wherein after brazing at a cooling rate of 18-30 ℃/min, the core layer has a main reinforced precipitation phase of AlCuMg atomic clusters and a nanoscale Al 2 CuMg transition phase after natural aging for 1-2 weeks, a micron-sized Al 2Cu/Al2 CuMg phase is absent, and the number density of micron-sized Mg 2Si/AlxCu4Mg5Si4 precipitates is lower than 100/mm 2.
8. An aluminum alloy composite panel as recited in claim 6, wherein the Zn element content in the upper barrier layer and the lower barrier layer satisfies: the potential difference between the upper barrier layer and the core layer is 40-150mV, and the potential difference between the lower barrier layer and the core layer is 40-150mV.
9. An aluminum alloy composite panel as recited in claim 6, wherein the aluminum alloy composite panel has a thickness of 0.6 to 2.0mm.
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