CN117070808B - Cast aluminum alloy suitable for brazing and preparation method and application thereof - Google Patents
Cast aluminum alloy suitable for brazing and preparation method and application thereof Download PDFInfo
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- CN117070808B CN117070808B CN202311337159.8A CN202311337159A CN117070808B CN 117070808 B CN117070808 B CN 117070808B CN 202311337159 A CN202311337159 A CN 202311337159A CN 117070808 B CN117070808 B CN 117070808B
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- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 102
- 238000005219 brazing Methods 0.000 title claims abstract description 76
- 238000002360 preparation method Methods 0.000 title abstract description 15
- 239000000956 alloy Substances 0.000 claims abstract description 108
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 106
- 238000005266 casting Methods 0.000 claims abstract description 97
- 229910052742 iron Inorganic materials 0.000 claims abstract description 57
- 239000002245 particle Substances 0.000 claims abstract description 49
- 229910052751 metal Inorganic materials 0.000 claims abstract description 26
- 239000002184 metal Substances 0.000 claims abstract description 26
- 239000011159 matrix material Substances 0.000 claims abstract description 25
- 230000005496 eutectics Effects 0.000 claims abstract description 22
- 238000004227 thermal cracking Methods 0.000 claims abstract description 22
- 210000001787 dendrite Anatomy 0.000 claims abstract description 11
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 11
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 8
- 238000001816 cooling Methods 0.000 claims description 32
- 239000012535 impurity Substances 0.000 claims description 28
- 239000000155 melt Substances 0.000 claims description 25
- 238000002844 melting Methods 0.000 claims description 24
- 230000008018 melting Effects 0.000 claims description 24
- 239000002994 raw material Substances 0.000 claims description 22
- 238000007670 refining Methods 0.000 claims description 22
- 238000000034 method Methods 0.000 claims description 19
- 238000005303 weighing Methods 0.000 claims description 16
- 230000008569 process Effects 0.000 claims description 10
- 229910052719 titanium Inorganic materials 0.000 claims description 9
- 229910052726 zirconium Inorganic materials 0.000 claims description 9
- 229910052749 magnesium Inorganic materials 0.000 claims description 7
- 229910052710 silicon Inorganic materials 0.000 claims description 6
- 239000010703 silicon Substances 0.000 claims description 6
- 239000000835 fiber Substances 0.000 claims description 5
- 239000011856 silicon-based particle Substances 0.000 claims description 5
- 238000003466 welding Methods 0.000 claims description 5
- 239000000203 mixture Substances 0.000 claims description 4
- 239000012752 auxiliary agent Substances 0.000 claims description 3
- 238000004519 manufacturing process Methods 0.000 claims description 3
- 239000007769 metal material Substances 0.000 claims description 2
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 abstract description 52
- 239000010949 copper Substances 0.000 abstract description 31
- 239000010936 titanium Substances 0.000 abstract description 10
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 abstract description 8
- 229910052802 copper Inorganic materials 0.000 abstract description 8
- -1 aluminum manganese Chemical compound 0.000 abstract description 5
- 229910000914 Mn alloy Inorganic materials 0.000 abstract description 3
- 238000003723 Smelting Methods 0.000 description 59
- 239000012071 phase Substances 0.000 description 45
- 239000003795 chemical substances by application Substances 0.000 description 23
- 230000000052 comparative effect Effects 0.000 description 23
- 239000011572 manganese Substances 0.000 description 20
- 238000010438 heat treatment Methods 0.000 description 14
- 238000005336 cracking Methods 0.000 description 13
- 229910018575 Al—Ti Inorganic materials 0.000 description 12
- 239000000463 material Substances 0.000 description 12
- 238000010586 diagram Methods 0.000 description 9
- QQHSIRTYSFLSRM-UHFFFAOYSA-N alumanylidynechromium Chemical compound [Al].[Cr] QQHSIRTYSFLSRM-UHFFFAOYSA-N 0.000 description 8
- 239000011651 chromium Substances 0.000 description 8
- 238000012360 testing method Methods 0.000 description 7
- 239000011777 magnesium Substances 0.000 description 6
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 5
- 239000007787 solid Substances 0.000 description 5
- 229910018580 Al—Zr Inorganic materials 0.000 description 4
- 229910052782 aluminium Inorganic materials 0.000 description 4
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 3
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 3
- 238000004512 die casting Methods 0.000 description 3
- 239000000945 filler Substances 0.000 description 3
- 239000007788 liquid Substances 0.000 description 3
- 238000012545 processing Methods 0.000 description 3
- 229910052761 rare earth metal Inorganic materials 0.000 description 3
- 238000007711 solidification Methods 0.000 description 3
- 230000008023 solidification Effects 0.000 description 3
- 229910018131 Al-Mn Inorganic materials 0.000 description 2
- 229910018461 Al—Mn Inorganic materials 0.000 description 2
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 2
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 2
- 238000004458 analytical method Methods 0.000 description 2
- 238000001514 detection method Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000005242 forging Methods 0.000 description 2
- 238000000265 homogenisation Methods 0.000 description 2
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 2
- 150000002910 rare earth metals Chemical class 0.000 description 2
- 230000009467 reduction Effects 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 229910052684 Cerium Inorganic materials 0.000 description 1
- 241000195482 Fucaceae Species 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 1
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical group [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- SAYOXHYAUHSWHN-UHFFFAOYSA-N alumane;manganese Chemical compound [AlH3].[AlH3].[Mn] SAYOXHYAUHSWHN-UHFFFAOYSA-N 0.000 description 1
- CSDREXVUYHZDNP-UHFFFAOYSA-N alumanylidynesilicon Chemical compound [Al].[Si] CSDREXVUYHZDNP-UHFFFAOYSA-N 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000004364 calculation method Methods 0.000 description 1
- GWXLDORMOJMVQZ-UHFFFAOYSA-N cerium Chemical compound [Ce] GWXLDORMOJMVQZ-UHFFFAOYSA-N 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000002950 deficient Effects 0.000 description 1
- 238000007872 degassing Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 230000014509 gene expression Effects 0.000 description 1
- 229910052746 lanthanum Inorganic materials 0.000 description 1
- FZLIPJUXYLNCLC-UHFFFAOYSA-N lanthanum atom Chemical compound [La] FZLIPJUXYLNCLC-UHFFFAOYSA-N 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 238000011056 performance test Methods 0.000 description 1
- 208000026438 poor feeding Diseases 0.000 description 1
- 230000001376 precipitating effect Effects 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 239000002893 slag Substances 0.000 description 1
- 239000007790 solid phase Substances 0.000 description 1
- 239000007858 starting material Substances 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 238000003756 stirring Methods 0.000 description 1
- 230000035882 stress Effects 0.000 description 1
- 230000002195 synergetic effect Effects 0.000 description 1
- 229910052718 tin Inorganic materials 0.000 description 1
- 239000011135 tin Substances 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 1
- 229910052725 zinc Inorganic materials 0.000 description 1
- 239000011701 zinc Substances 0.000 description 1
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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/026—Alloys based on aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/03—Making non-ferrous alloys by melting using master alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/06—Making non-ferrous alloys with the use of special agents for refining or deoxidising
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Continuous Casting (AREA)
- Manufacture And Refinement Of Metals (AREA)
Abstract
The invention discloses a cast aluminum alloy suitable for brazing and a preparation method and application thereof, wherein iron, copper, M1 and M2 elements are added on the basis of an aluminum manganese alloy system to form an aluminum-manganese-iron-copper-M1-M2 alloy system, M1 is Ti and/or Zr, and M2 is at least one selected from V, mo and Cr, so that an alloy structure can have a eutectic structure with high thermal stability on an alpha-Al matrix and can separate out dispersed particles with the size of 0.1-5 mu M from the alpha-Al matrix at high temperature, the size of the alpha-Al matrix, the secondary dendrite wall spacing and the area and the size of the eutectic structure are further controlled, the aluminum alloy has good fluidity, low thermal cracking property, good feeding property and high-temperature stability, and the uniformity of casting manufacturability and high-temperature brazing performance is realized, and the current requirements for high-temperature brazing cast aluminum alloy can be brazed at high temperature to prepare metal products.
Description
Technical Field
The invention relates to the technical field of cast aluminum alloy, in particular to cast aluminum alloy suitable for brazing and a preparation method and application thereof.
Background
At present, valve bodies of a water-cooling/liquid-cooling radiator of electronic equipment and a new energy automobile heat management system are all made of aluminum alloy materials, and the products are generally formed by forging 6000 series aluminum alloy, machining and then brazing with 3000 series or 6000 series plates, however, the production process flow of a forging piece is long, complex components cannot be prepared, the effective yield is low, and the product cost is high. At present, casting is taken as a near-net forming technology, forming of thin-wall, complex-structure and high-precision parts can be realized, the preparation of the parts can be completed only by small amount of processing or even no processing, and the casting is expected to be used for casting aluminum alloy, however, practice finds that the solidus temperature of the aluminum-silicon cast aluminum alloy which is currently mainstream is generally below 580 ℃ and cannot meet the requirement of brazing temperature 590-610 ℃ (brazing refers to a welding method for filling gaps of solid workpieces with liquid brazing filler metal to connect metals after brazing filler metal and weldments are heated to the melting temperature of the brazing filler metal at the same time).
The aluminum-manganese aluminum alloy has the characteristics of high corrosion resistance and high melting point, can be applied to the field of brazing, is limited by a component system at present, can be produced only by direct water-cooling semi-continuous casting (DC casting), homogenizing and rolling processes, has high hot cracking tendency and is easy to crack if the existing alloy components are directly adopted for casting, and part of alloy formula is matched with additional processing processes, so that the whole process becomes more complicated, the requirements on process conditions are possibly higher, and the control is difficult; for example: (1) The invention patent application CN113897519A discloses an aluminum-manganese-magnesium-silicon-titanium-tin casting alloy for realizing brazing by vacuum die casting and a preparation method thereof, wherein magnesium and silicon are added on the basis of aluminum-manganese eutectic composition, the toughness of the alloy is improved on the basis of not reducing the heat conducting property of the alloy, and titanium and tin are added to refine grains, so that the toughness of the alloy is improved; however, the addition of magnesium and silicon can obviously increase the solidification zone, exacerbate the hot cracking tendency, and the alloy needs to be subjected to homogenization treatment before brazing to eliminate the low-melting-point phase generated in the solidification process, so that the process is relatively complicated; (2) The invention patent application CN115679159A discloses an aluminum-nickel-manganese alloy material for high-temperature brazing and a rheologic die casting forming method thereof, wherein the casting performance is improved by adding nickel and manganese, and meanwhile shrinkage and hot cracks are relieved by rheologic die casting, but the rheologic process is difficult to control in actual operation, and defective products are easy to occur.
Furthermore, the invention patent application CN116377262a discloses a method for manufacturing a high pressure casting aluminum alloy which can be used for brazing, comprising: melting the regenerated aluminum raw material, and controlling the temperature of the aluminum liquid to be between 710 and 730 ℃; wherein the aluminum liquid comprises: up to 0.5 wt% silicon, up to 0.5 wt% iron, up to 0.3 wt% copper, up to 0.3 wt% zinc, 0.6 to 1.5 wt% manganese, up to 0.2 wt% chromium, 0.3 to 1.0 wt% magnesium, up to 0.05 wt% titanium, 5.0 to 12.0 wt% rare earth; refining and casting aluminum alloy; the aluminum alloy in the patent has complex components, contains a large amount of rare earth elements (lanthanum and cerium), and has high cost.
Disclosure of Invention
The invention aims to overcome one or more defects in the prior art, and provides an improved braze-welded cast aluminum alloy which has the advantages of small hot cracking tendency, good fluidity and good feeding capability, and the alloy can be used for directly casting complex structural parts, can be used for braze-welded assembly without homogenization, and has relatively low cost.
The invention also provides a preparation method of the casting aluminum alloy suitable for brazing and application of the casting aluminum alloy in preparation of metal products.
In order to achieve the above purpose, the invention adopts a technical scheme that:
a cast aluminum alloy suitable for brazing, the alloy structure of the cast aluminum alloy comprising an a-Al matrix and a eutectic structure;
wherein the size of the alpha-Al matrix is less than or equal to 150 mu m, and the secondary dendrite wall spacing is less than or equal to 30 mu m; the alpha-Al matrix can separate out dispersed particles with thermal stability in the brazing process, the size of the dispersed particles is 0.1-5 mu m, and the dispersed particles comprise Al 3 M1 particles, al 6 (Fe, mn, M2) particles, the number density of the dispersed particles being 10 6 ~10 10 Individual/cm 2 ；
The eutectic structure comprises alpha-Al phase and Al 6 (Fe, mn) phase, al 6 (Fe, mn, M2) phase and Al 6 (Fe, mn, cu, M2) phase, said Al 6 (Fe, mn) phase, the Al 6 (Fe, mn, M2) phase, the Al 6 The (Fe, mn, cu, M2) phase independently has a size of 1 to 50 μm;
the area of the eutectic structure accounts for 1/10-3/10 of the area of the alloy structure;
m1 is one or two selected from Ti and Zr, and M2 is one or more selected from V, mo and Cr.
Al is an aluminum element, mn is a manganese element, fe is an iron element, cu is a copper element, ti is a titanium element, zr is a zirconium element, V is a vanadium element, mo is a molybdenum element, and Cr is a chromium element.
According to some preferred aspects of the invention, the Al 6 (Fe, mn) phase, the Al 6 (Fe, mn, M2) phase, the Al 6 The shape of the (Fe, mn, cu, M2) phase includes bulk, short fiber, and worm, respectively, independently.
The bulk, short fiber and worm shapes described in the present invention are all common expressions for crystalline phase shapes in the art, and are not described in detail herein.
Further, the Al 6 (Fe, mn) phase, the Al 6 (Fe, mn, M2) phase or said Al 6 In the (Fe, mn, cu, M2) phase, the eutectic phase with short fiber shape and worm shape accounts for more than 80 percent in total.
Further, in some embodiments, the dispersed particles further comprise Al 6 (Fe, mn) particles, al 6 One or two of (Fe, mn, cu, M2) particles.
Further, when the composition of the cast aluminum alloy contains silicon as an impurity, the dispersed particles further include α -Al (Fe, mn, M2) Si particles and/or α -Al (Fe, mn, cu, M2) Si particles.
According to some preferred and specific aspects of the present invention, the average size of the α -Al matrix is 20-120 μm, the average value of the secondary dendrite wall spacing is 5-30 μm, and the degree of grain refinement is controlled, which is advantageous in reducing the tendency to heat cracking.
According to some preferred and specific aspects of the invention, the dispersed particles have an average size of 0.1-3 μm.
According to some preferred and specific aspects of the invention, the dispersed particles have a number density of 10 7 ~10 10 Individual/cm 2 。
According to some preferred and specific aspects of the present invention, the cast aluminum alloy comprises the following components in mass percent:
Mn 1.0~3.0%
Fe 0.1~1.0%
Cu 0.05~1.0%
M1 0.02~0.6%
M2 0.02~1.0%，
the balance being Al and unavoidable impurities.
In some embodiments of the present invention, the cast aluminum alloy comprises the following components in mass percent:
Mn 1.0~2.8%
Fe 0.1~1.0%
Cu 0.05~0.7%
M1 0.02~0.4%
M2 0.02~0.8%，
the balance being Al and unavoidable impurities.
In some embodiments of the present invention, the cast aluminum alloy comprises the following components in mass percent:
Mn 1.0~2.8%
Fe 0.1~0.8%
Cu 0.05~0.7%
M1 0.02~0.4%
M2 0.02~0.6%，
the balance being Al and unavoidable impurities.
In some embodiments of the invention, M1 is composed of Ti and Zr. Further, according to some preferred and specific aspects of the present invention, when M1 is composed of Ti and Zr, ti is 0.02% to 0.25% by mass of the cast aluminum alloy, and Zr is 0.002% to 0.20% by mass of the cast aluminum alloy.
In some embodiments of the invention, M2 consists of V, mo, cr. Further, according to some preferred and specific aspects of the present invention, when M2 is composed of V, mo, cr, V is 0.003% -0.20% by mass of the cast aluminum alloy, mo is 0.001% -0.20% by mass of the cast aluminum alloy, and Cr is 0.002% -0.20% by mass of the cast aluminum alloy.
According to some preferred and specific aspects of the present invention, the content of the impurity in the cast aluminum alloy is controlled to be less than 0.2% in mass percent.
Further, the content of the impurity in the cast aluminum alloy is controlled to be less than 0.1% in terms of mass percent.
In some embodiments of the invention, the impurities include one or more of Mg, si, zn. In the present invention, the impurity content including Mg, si, zn should be controlled as much as possible.
According to some preferred and specific aspects of the present invention, a method of preparing the cast aluminum alloy comprises:
weighing the components according to the formula amount, and melting to obtain a melt;
adding a refining auxiliary agent into the melt, and refining to obtain a metal melt;
cooling the metal melt to obtain the cast aluminum alloy; wherein the cooling rate of the cooling is controlled to be more than or equal to 2 ℃/s.
In some embodiments of the invention, the cooling rate of the cooling is controlled to be 2-50 ℃/s.
In some embodiments of the invention, the refining aid comprises a solid refining agent and a refining agent.
Further, the solid refining agent may be of the rare earth refining agent, sodium-free refining agent or the like. Still further, in some embodiments of the present invention, the solid refining agent is added in an amount of 0.005% to 0.5% by mass of the melt.
Further, the refiner may be of the type Al-Ti-B, al-Ti-C, al-Ti-C-B, etc. Still further, in some embodiments of the present invention, the refiner is added in an amount of 0.008% to 1.0% by mass of the melt.
According to some specific aspects of the invention, the cast aluminum alloy has a thermal cracking coefficient of less than 50. Further, according to the present invention, the cast aluminum alloy has a thermal cracking coefficient of 45 or less.
In the invention, the melting point of the cast aluminum alloy can reach 600-650 ℃.
Further, according to the present invention, the cast aluminum alloy has a tensile strength of 145MPa or more, a yield strength of 75MPa or more, and an elongation of 12% or more at room temperature in an as-cast state.
Further, according to the present invention, after brazing, the cast aluminum alloy has a tensile strength of 140MPa or more, a yield strength of 70MPa or more, and an elongation of 12% or more at room temperature.
The invention provides another technical scheme that: a cast aluminum alloy suitable for brazing, the cast aluminum alloy comprising, in mass percent:
Mn 1.0~3.0%
Fe 0.1~1.0%
Cu 0.05~1.0%
M1 0.02~0.6%
M2 0.02~1.0%，
the balance of Al and unavoidable impurities, M1 is one or a combination of two selected from Ti and Zr, and M2 is one or a combination of a plurality of selected from V, mo and Cr.
The invention provides another technical scheme that: a method of preparing the cast aluminum alloy suitable for brazing described above, the method comprising: weighing the components according to the formula amount, melting to obtain a melt, adding a refining auxiliary agent into the melt, refining to obtain a metal melt, and cooling the metal melt to obtain the cast aluminum alloy; wherein the cooling rate of the cooling is controlled to be more than or equal to 2 ℃/s.
The invention provides another technical scheme that: an aluminum alloy casting which is produced by melting and casting the cast aluminum alloy suitable for brazing, or by melting and refining the raw material components of the cast aluminum alloy suitable for brazing.
In some embodiments of the present invention, in preparing the cast aluminum alloy suitable for brazing or the aluminum alloy casting, the alloying elements of each component in the raw material may be added in the form of a pure alloy or a master alloy.
The invention provides another technical scheme that: a metal product is obtained by casting a metal melt, and the metal product is manufactured by welding the casting and other metal materials in a brazing mode;
the metal melt is prepared by melting the casting aluminum alloy suitable for brazing, or is prepared by melting and refining the raw material components of the casting aluminum alloy suitable for brazing;
and controlling the cooling rate to be more than or equal to 2 ℃/s in the casting process.
In some embodiments of the invention, the brazing has a welding temperature of 590-620 ℃.
Due to the application of the technical scheme, compared with the prior art, the invention has the following advantages:
in order to meet the current requirement for high-temperature brazing casting aluminum alloy, the problems of poor casting formability, large hot cracking tendency, poor feeding and the like commonly existing in the current high-melting-point casting alloy are solved. Based on a great deal of experimental study, the inventor unexpectedly found that iron, copper, M1 (Ti and/or Zr) and M2 (at least one of V, mo and Cr) elements are added on the basis of an aluminum-manganese alloy system to form an aluminum-manganese-iron-copper-M1-M2 alloy system, when the alloy structure can be provided with a eutectic structure with high thermal stability on an alpha-Al matrix (comprising alpha-Al phase and Al phase) 6 (Fe, mn) phase+Al 6 (Fe, mn, M2) phase+Al 6 (Fe, mn, cu, M2) phase) capable of precipitating dispersed particles (at least comprising Al) of 0.1-5 μm in size from an alpha-Al matrix at high temperature 3 M1 particles, al 6 (Fe, mn, M2) particles), the size of the alpha-Al matrix, the secondary dendrite wall spacing, the area of eutectic structures and the eutectic phase size are further controlled, so that the aluminum alloy has good fluidity, low thermal cracking property, good feeding property and high-temperature stability, and the casting manufacturability and high-temperature brazeability are unified;
through further mechanism studies, the analysis considered that: the invention can form dispersed particles with specific size and density, on one hand, the high-temperature stability is good, the temperature resistance of the system can be improved, on the other hand, the mechanical property of the alloy can be improved, and aging and solid solution heat treatment are not needed, so that the strength after brazing is further ensured;
meanwhile, by adding a certain amount of Fe element into the Al-Mn base alloy, the eutectic structure of the alloy is formed by alpha-Al phase and Al phase 6 Mn phase is converted into alpha-Al phase and Al phase 6 (Fe, mn) phase, realize eutectic structure refinement;
the addition of Cu element can widen the effective feeding temperature interval, cu atoms are in solid solution in alpha-Al, the strength of a casting can be improved, meanwhile, the addition of Cu element is also beneficial to the precipitation of dispersed particles, the number density of the dispersed particles is increased, and the growth degree of the dispersed particles can be controlled, so that the dispersed particles tend to grow into a relatively smaller size;
the M1 element is added, so that the quantity of alpha-Al matrix nucleation points can be increased, and grain refinement is realized; can haveEffectively delaying dendrite bridging time and delaying solidification fraction when stress is formed; the number of the bypass dendrites can be increased, the bypass strength is improved, and the thermal cracking property is reduced; formation of Al in alpha-Al matrix 3 M1 is used for dispersing particles, so that the mechanical properties of the alloy are improved;
m2 element is added, on one hand, al can be further realized 6 (Fe, mn) phase transition to Al 6 (Fe, mn, M2) phase and Al 6 (Fe, mn, cu, M2) phase, improving the thermal stability of the eutectic phase, further improving the morphology of the second phase, on the other hand, forming Al in the alpha-Al matrix 6 (Fe, mn, M2) and optionally Al 6 (Fe, mn, cu, M2) dispersing particles, so as to improve the mechanical properties of the alloy;
furthermore, by the synergistic effect of various eutectic phases, the alloy has good fluidity and feeding property and can inhibit hot cracking while ensuring high melting point and high strength, so that the alloy can ensure good fluidity and low hot cracking under the casting and filling conditions, and the dispersed particles which can be separated from the alpha-Al matrix at high temperature can further ensure excellent welding performance in the high-temperature brazing process.
Drawings
FIG. 1 is a metallographic structure (200 times magnification) of a casting obtained in example 1 of the present invention;
FIG. 2 is a metallographic structure (500 times magnification) of the casting obtained in example 1 of the present invention;
FIG. 3 is a scanning structure diagram of the cast product obtained in example 1 of the present invention after brazing;
FIG. 4 is a scanning structure diagram of the cast product obtained in example 9 of the present invention after brazing;
FIG. 5 is a scanning structure diagram of the casting obtained in comparative example 1 of the present invention after brazing;
FIG. 6 is a metallographic structure (at 1000 magnification) of the casting obtained in comparative example 4 of the present invention;
FIG. 7 is a metallographic view showing the weld joint of the cast article obtained in example 1 of the present invention after brazing;
FIG. 8 is a schematic illustration of a thermal cracking test of castings according to an embodiment of the present invention;
FIG. 9 is a graph showing the results of the thermal cracking tests of examples 1, 2 and 3 according to the present invention.
Detailed Description
The above-described aspects are further described below in conjunction with specific embodiments; it should be understood that these embodiments are provided to illustrate the basic principles, main features and advantages of the present invention, and that the present invention is not limited by the scope of the following embodiments; the implementation conditions employed in the examples may be further adjusted according to specific requirements, and the implementation conditions not specified are generally those in routine experiments.
All starting materials are commercially available or prepared by methods conventional in the art, not specifically described in the examples below.
In the following, in order to test the brazing performance of the cast aluminum alloy, the test is performed after the cast aluminum alloy is directly cast into an aluminum alloy casting in the aluminum alloy forming process, and the difference between the two is that: the aluminum alloy is formed by directly cooling the melt refined by each component, and the aluminum alloy casting is formed by casting the melt refined by each component according to a preset shape and then cooling, so that the performance of the aluminum alloy casting can be reflected by the performance of the aluminum alloy casting.
In the art, the pre-designed amount of the aluminum alloy casting during preparation may have a certain error with the actual detection value at the later stage, wherein the detection value after casting is finished is taken as a reference, and the content of each metal is measured by a direct-reading spectrometer.
Example 1:
the example provides an aluminum alloy casting and a preparation method thereof, and the preparation method of the aluminum alloy casting comprises the following steps:
(1) Weighing industrial pure Al ingot, al-Mn intermediate alloy, fe agent and pure Cu wire according to a set amount, placing the materials into a smelting furnace, heating to 790+/-10 ℃, cooling the smelting furnace to 750+/-10 ℃ after raw materials in the smelting furnace are melted, and then adding other intermediate alloy: adding the Al-Ti intermediate alloy and the Al-V intermediate alloy into a smelting furnace respectively to be completely melted to obtain a melt;
(2) The melt is kept at 750+/-10 ℃, a solid refining agent (specifically, coveral78 of Fucaceae) and a refining agent (specifically, shenzhen New star Al-Ti5-B refining agent) accounting for 2 per mill of the mass of the melt are respectively added into a smelting furnace, stirring and degassing are carried out for 20min by adopting a rotary rotor, and slag is removed after standing for 20min, so as to obtain refined metal melt;
(3) When the temperature of the metal melt is 740+/-10 ℃, pouring the metal melt into a preheated steel mould at 175+/-10 ℃ to obtain a casting; wherein the cooling rate of the casting during casting is about 4+ -1deg.C/s.
The casting obtained in the embodiment comprises the following components in percentage by mass: mn:1.9%; fe:0.5%; cu:0.4%; ti:0.096%; zr:0.002%; v:0.045%; mo:0.002%; cr:0.005% of Al and the balance of unavoidable impurities.
Example 2:
substantially the same as in example 1, the only difference is that: the step (1) is as follows: weighing industrial pure Al ingot, al-Mn intermediate alloy, fe agent and pure Cu wire according to a set amount, placing the materials into a smelting furnace, heating to 790+/-10 ℃, cooling the smelting furnace to 750+/-10 ℃ after raw materials in the smelting furnace are melted, and then adding other intermediate alloy: adding the Al-Ti intermediate alloy and the Al-V intermediate alloy into a smelting furnace respectively to be completely melted to obtain a melt;
steps (2) and (3) are the same as in example 1;
the casting obtained in the embodiment comprises the following components in percentage by mass: mn:2.8%; fe:0.4%; cu:0.3%; ti:0.10%; zr:0.002%; v:0.055%; mo:0.002%; cr:0.005% of Al and the balance of unavoidable impurities.
Example 3:
substantially the same as in example 1, the only difference is that: the step (1) is as follows: weighing industrial pure Al ingot, al-Mn intermediate alloy, fe agent and pure Cu wire according to a set amount, placing the materials into a smelting furnace, heating to 790+/-10 ℃, cooling the smelting furnace to 750+/-10 ℃ after raw materials in the smelting furnace are melted, and then adding other intermediate alloy: adding the Al-Ti intermediate alloy and the Al-V intermediate alloy into a smelting furnace respectively to be completely melted to obtain a melt;
steps (2) and (3) are the same as in example 1;
the casting obtained in the embodiment comprises the following components in percentage by mass: mn:1.4%; fe:0.4%; cu:0.4%; ti:0.1%; zr:0.002%; v:0.044%; mo:0.002%; cr:0.005% of Al and the balance of unavoidable impurities.
Example 4:
substantially the same as in example 1, the only difference is that: the step (1) is as follows: weighing industrial pure Al ingot, al-Mn intermediate alloy, fe agent and pure Cu wire according to a set amount, placing the materials into a smelting furnace, heating to 790+/-10 ℃, cooling the smelting furnace to 750+/-10 ℃ after raw materials in the smelting furnace are melted, and then adding other intermediate alloy: adding the Al-Ti intermediate alloy, the Al-V intermediate alloy and the Al-Cr intermediate alloy into a smelting furnace respectively for complete smelting to obtain a melt;
steps (2) and (3) are the same as in example 1;
the casting obtained in the embodiment comprises the following components in percentage by mass: mn:2.0%; fe:0.5%; cu:0.1%; ti:0.092%; zr:0.002%; v: 0.024; mo:0.002%; cr:0.055%, the balance of Al and unavoidable impurities.
Example 5:
substantially the same as in example 1, the only difference is that: the step (1) is as follows: weighing industrial pure Al ingot, al-Mn intermediate alloy, fe agent and pure Cu wire according to a set amount, placing the materials into a smelting furnace, heating to 790+/-10 ℃, cooling the smelting furnace to 750+/-10 ℃ after raw materials in the smelting furnace are melted, and then adding other intermediate alloy: adding the Al-Ti intermediate alloy, the Al-V intermediate alloy and the Al-Cr intermediate alloy into a smelting furnace respectively for complete smelting to obtain a melt;
steps (2) and (3) are the same as in example 1;
the casting obtained in the embodiment comprises the following components in percentage by mass: mn:2.1%; fe:0.5%; cu:0.7%; ti:0.078%; zr:0.003%; v: 0.023; mo:0.001%; cr:0.045%, the balance of Al and unavoidable impurities.
Example 6:
substantially the same as in example 1, the only difference is that: the step (1) is as follows: weighing industrial pure Al ingot, al-Mn intermediate alloy, fe agent and pure Cu wire according to a set amount, placing the materials into a smelting furnace, heating to 790+/-10 ℃, cooling the smelting furnace to 750+/-10 ℃ after raw materials in the smelting furnace are melted, and then adding other intermediate alloy: adding the Al-Ti intermediate alloy, the Al-V intermediate alloy and the Al-Mo intermediate alloy into a smelting furnace respectively for complete smelting to obtain a melt;
steps (2) and (3) are the same as in example 1;
the casting obtained in the embodiment comprises the following components in percentage by mass: mn:2.4%; fe:0.5%; cu:0.4%; ti:0.16%; zr:0.002%; v:0.18%; mo:0.08%; cr:0.002%, the balance being Al and unavoidable impurities.
Example 7:
substantially the same as in example 1, the only difference is that: the step (1) is as follows: weighing industrial pure Al ingot, al-Mn intermediate alloy, fe agent and pure Cu wire according to a set amount, placing the materials into a smelting furnace, heating to 790+/-10 ℃, cooling the smelting furnace to 750+/-10 ℃ after raw materials in the smelting furnace are melted, and then adding other intermediate alloy: adding the Al-Ti intermediate alloy, the Al-Zr intermediate alloy, the Al-V intermediate alloy and the Al-Cr intermediate alloy into a smelting furnace respectively for complete melting to obtain a melt;
steps (2) and (3) are the same as in example 1;
the casting obtained in the embodiment comprises the following components in percentage by mass: mn:2.4%; fe:0.6%; cu:0.4%; ti:0.04%; zr:0.05%; v:0.18%; mo:0.003%; cr:0.15% of Al and the balance of unavoidable impurities.
Example 8:
substantially the same as in example 1, the only difference is that: the step (1) is as follows: weighing industrial pure Al ingot, al-Mn intermediate alloy, fe agent and pure Cu wire according to a set amount, placing the materials into a smelting furnace, heating to 790+/-10 ℃, cooling the smelting furnace to 750+/-10 ℃ after raw materials in the smelting furnace are melted, and then adding other intermediate alloy: adding the Al-Ti intermediate alloy, the Al-Zr intermediate alloy, the Al-Mo intermediate alloy and the Al-Cr intermediate alloy into a smelting furnace respectively for complete melting to obtain a melt;
steps (2) and (3) are the same as in example 1;
the casting obtained in the embodiment comprises the following components in percentage by mass: mn:2.4%; fe:0.5%; cu:0.4%; ti:0.15%; zr:0.13%; v:0.003%; mo:0.12%; cr:0.19%, the balance being Al and unavoidable impurities.
Example 9:
substantially the same as in example 1, the only difference is that: the step (1) is as follows: weighing industrial pure Al ingot, al-Mn intermediate alloy, fe agent and pure Cu wire according to a set amount, placing the materials into a smelting furnace, heating to 790+/-10 ℃, cooling the smelting furnace to 750+/-10 ℃ after raw materials in the smelting furnace are melted, and then adding other intermediate alloy: adding an Al-Ti intermediate alloy, an Al-Zr intermediate alloy, an Al-V intermediate alloy, an Al-Mo intermediate alloy and an Al-Cr intermediate alloy into a smelting furnace respectively for complete smelting to obtain a melt;
steps (2) and (3) are the same as in example 1;
the casting obtained in the embodiment comprises the following components in percentage by mass: mn:2.2%; fe:0.6%; cu:0.3%; ti:0.02%; zr:0.1%; v:0.15%; mo:0.11%; cr:0.24%, the balance of Al and unavoidable impurities.
Comparative example 1:
substantially the same as in example 1, the only difference is that: the step (1) is as follows: weighing industrial pure Al ingot, al-Mn intermediate alloy, fe agent and pure Cu wire according to a set amount, placing the materials into a smelting furnace, heating to 790+/-10 ℃, cooling the smelting furnace to 750+/-10 ℃ after raw materials in the smelting furnace are melted, and then adding other intermediate alloy: adding Al-Cr intermediate alloy into a smelting furnace respectively to be completely melted to obtain a melt;
steps (2) and (3) are the same as in example 1;
the casting components obtained in the comparative example comprise the following components in percentage by mass: mn:1.8%; fe:0.4%; cu:0.3%; ti:0.002%; zr:0.002%; v:0.001%; mo:0.002%; cr:0.05%, the balance of Al and unavoidable impurities.
In the preparation process of the casting, M1 element is not added, and Ti and Zr contained in the obtained casting component are derived from trace components contained in other raw materials.
Comparative example 2:
substantially the same as in example 1, the only difference is that: the step (1) is as follows: weighing industrial pure Al ingot, al-Mn intermediate alloy, fe agent and pure Cu wire according to a set amount, placing the materials into a smelting furnace, heating to 790+/-10 ℃, cooling the smelting furnace to 750+/-10 ℃ after raw materials in the smelting furnace are melted, and then adding other intermediate alloy: adding the Al-Ti intermediate alloy and the Al-Zr intermediate alloy into a smelting furnace respectively to be completely melted to obtain a melt;
steps (2) and (3) are the same as in example 1;
the casting components obtained in the comparative example comprise the following components in percentage by mass: mn:1.9%; fe:0.5%; cu:0.2%; ti:0.08%; zr:0.05%; v:0.001%; mo:0.003%; cr:0.002%, the balance being Al and unavoidable impurities.
In the preparation process of the casting, M2 element is not added, and V, mo and Cr contained in the obtained casting components are derived from trace components contained in other raw materials.
Comparative example 3:
substantially the same as in example 1, the only difference is that: the step (1) is as follows: weighing industrial pure Al ingot, al-Mn intermediate alloy, fe agent and pure Cu wire according to a set amount, placing the materials into a smelting furnace, heating to 790+/-10 ℃, cooling the smelting furnace to 750+/-10 ℃ after raw materials in the smelting furnace are melted, and then adding other intermediate alloy: adding the Al-Ti intermediate alloy, the Al-V intermediate alloy and the Al-Cr intermediate alloy into a smelting furnace respectively for complete smelting to obtain a melt;
steps (2) and (3) are the same as in example 1;
the casting components obtained in the comparative example comprise the following components in percentage by mass: mn:2.1%; fe:0.5%; cu:1.1%; ti:0.08%; zr:0.002%; v:0.02%; mo:0.001%; cr:0.045%, the balance of Al and unavoidable impurities.
In this example, an excessive amount of Cu was added during the preparation.
Comparative example 4:
substantially the same as in example 1, the only difference is that: the step (1) is as follows: weighing industrial pure Al ingot, al-Mn intermediate alloy and Fe agent according to a set amount, placing the industrial pure Al ingot, the Al-Mn intermediate alloy and the Fe agent into a smelting furnace, heating to 790+/-10 ℃, cooling the smelting furnace to 750+/-10 ℃ after raw materials in the smelting furnace are melted, and then adding other intermediate alloy: adding the Al-Ti intermediate alloy, the Al-V intermediate alloy and the Al-Cr intermediate alloy into a smelting furnace respectively for complete smelting to obtain a melt;
steps (2) and (3) are the same as in example 1;
the casting components obtained in the comparative example comprise the following components in percentage by mass: mn:2.0%; fe:0.5%; cu:0.002%; ti:0.08%; zr:0.002%; v:0.02%; mo:0.001%; cr:0.04%, the balance of Al and unavoidable impurities.
In this example, cu is not added in the preparation process, and Cu contained in the obtained casting component should be derived from trace components contained in other raw materials.
Performance test:
(1) Metallographic structure diagrams of the casting obtained in the example 1 under different magnifications are shown in fig. 1 and 2 respectively; as can be seen from fig. 1 and 2, the provided alloy structure in the casting formed by casting alloy A1-Mn-Fe-Cu-M1-M2 is composed of α -Al matrix + eutectic structure, wherein the α -Al matrix is mainly dendritic and equiaxed, the average size of the α -Al matrix is about 80 μm, and the average value of the secondary dendrite wall spacing is about 21 μm; eutectic structure is composed of alpha-Al phase and Al 6 (Fe, mn) phase+Al 6 (Fe, mn, cu, M2) phase +Al 6 The (Fe, mn, M2) phase is composed of, in percent, about 18% of the area of the eutectic structure; analysis and statistics of the above cast structure show that the second phase in the structure is mainly massive, short fiber-like and worm-like Al with the size of 1-30 μm 6 (Fe, mn) phase, al 6 (Fe, mn, cu, M2) phase, al 6 (Fe, mn, M2) phases, which can form a three-dimensional continuous network structure, can realize the reinforcement and high-temperature stability of the alloy.
The scanning structure diagram of the cast product of example 1 after brazing is shown in FIG. 3, and it can be seen that after brazing, dispersed particles including Al are precipitated in the alpha-Al matrix 3 M1 particles, al 6 (Fe, mn) particles, al 6 (Fe, mn, cu, M2) particles, al 6 The presence of (Fe, mn, M2) particles, alpha-Al (Fe, mn, cu, M2) Si particles, etc., means that the composition may contain small amounts of silicon impurities, which are dispersed in the flat form of particlesThe average size is about 0.5 μm, and the number density is 3.2X10 8 Individual/cm 2 。
As can be seen from fig. 4, the scanning structure diagram of the cast product of example 9 after brazing treatment is shown in fig. 4, and as the addition amount of M1 (Zr, ti) element increases in example 9, the number of dispersed particles increases further, which means that the M1 (Zr, ti) element significantly affects the precipitation and precipitation amount of dispersed particles, and grains are finer.
As is clear from FIG. 5, the scanning structure diagram of the brazing treated casting of comparative example 1 is shown in FIG. 5, and it is clear from FIG. 5 that Al cannot be formed in comparative example 1 because M1 element is not added 3 M1 dispersed particles, the number of dispersed particles is very small (the number is less than 1×10 6 Individual/cm 2 ) The size is larger, the purpose of grain refinement cannot be achieved, and meanwhile, the average size of an alpha-Al matrix and the average value of secondary dendrite wall spacing are also larger, so that the final thermal cracking performance is poor, and the strength after brazing is also insufficient.
The metallographic structure diagram of the casting obtained in comparative example 4 at a magnification of 1000 times is shown in fig. 6, and it is clear from fig. 6 that in comparative example 4, since Cu element is not added, the effective feeding temperature interval is extremely narrow, so that feeding is insufficient in the casting process, shrinkage porosity is formed, and the mechanical properties are adversely affected.
In addition, the metallographic structure diagram of the welded seam of the casting obtained in the embodiment 1 is shown in fig. 7, and the metallographic structure of the welded seam of the casting in fig. 7 shows that the casting obtained in the embodiment 1 is well combined with the brazing composite plate after brazing, the welded seam is full and uniform, no local grain boundary is melted in the casting, no obvious deformation exists, and the requirements of the product on the connection strength and the air tightness are ensured.
(2) And calculating the theoretical melting point of each aluminum alloy casting by using phase diagram software according to the actual measurement components of each aluminum alloy casting. And testing the room temperature mechanical property of the aluminum alloy casting by using an electronic universal testing machine. The hot cracking tendency of the aluminum alloy castings is evaluated by a hot cracking rod method, and the method is specifically as follows: the hot cracking tendency of aluminum alloy castings, i.e., the length of the rod from which the hot cracks are generated, the location of the hot cracks, and the size of the hot cracks, are mainly examined in three aspects. The thermal cracking coefficient (HCS) calculation method is as follows:
HCS=∑(f length *f location *w crack )
wherein f length As the rod length influencing factor, according to the difficulty in occurrence of thermal cracking, the rod length influencing factor is shown in the left side (I) of fig. 8, and capital letters respectively represent rods of different lengths, wherein the rod length influencing factor of the longest rod D is 4, the next-long rod C is 8, the shorter rod B is 16, and the shortest rod a is 32.f (f) location As for the crack position influencing factor, the parameters are shown on the right side (II) of fig. 8, the lower case letters respectively represent different fracture positions, the crack is most likely to occur at the root a, the parameter is 1, the parameter is 2 at the ball end c, the middle position b is least likely to fracture, and the parameter is 3.W (W) crack The crack size factor was 4 at break, 3 at half break, 2 at hairline and 1 at half hairline. Taking the thermal cracking test results of example 1, comparative example 2 and comparative example 3 as examples, and the example shows fig. 9, it is obvious that the thermal cracking tendency of the aluminum alloy castings obtained in the examples of the present invention is very small, and the thermal cracking coefficient (HCS) of comparative examples 1 to 3 is 6 to 8 times that of example 1, and the thermal cracking property is significantly improved compared with that of the examples.
The structural characteristics, theoretical melting point, thermal cracking result and room temperature tensile properties of the aluminum alloy castings obtained in the above examples and comparative examples are shown in tables 1 and 2, wherein table 1 is the statistical result of the structural characteristics of each alloy casting, and table 2 is the melting point, thermal cracking result and room temperature mechanical property of each alloy casting.
Note that: the brazing conditions are as follows: 605℃for 15min.
As can be seen from tables 1-2, the theoretical melting point of the casting of the A1-Mn-Fe-Cu-M1-M2 casting alloy provided by the invention is generally higher than the brazing temperature by 30-40 ℃ and is close to 3003 alloy, the brazing requirement is completely met, and as can be seen by combining with figures 3 and 4, the structure after brazing is relatively stable, and a large amount of dispersed phases are precipitated in crystals, so that the performance of the casting is not greatly changed after brazing.
From the thermal cracking coefficient point of view, the thermal cracking resistance of the alloy can be effectively controlled by adding proper Mn, refining the primary Mn-containing phase by adopting Fe and adding proper amounts of M1 elements (Ti, zr) and M2 elements (V, mo and Cr). From the mechanical property, the tensile strength of the casting of the A1-Mn-Fe-Cu-M1-M2 casting alloy provided by the invention is more than 145MPa, the yield strength is more than 75MPa, the elongation is more than 15%, the tensile strength after brazing is still more than 145MPa, the yield strength is more than 70MPa, the elongation is more than 16%, and the yield strength of the conventional 3003 alloy brazing is only 40-50MPa, so that the A1-Mn-Fe-Cu-M1-M2 casting alloy provided by the invention has certain mechanical property advantages;
the comparative example 1 does not add M1 element, the thermal cracking coefficient is increased sharply and reaches 96, and the performance after brazing is reduced obviously, which shows that after the M1 element is absent, the alpha-Al matrix has insufficient dispersed particles and fewer types and poorer sizes, and the average size of the alpha-Al matrix and the secondary dendrite wall spacing are larger as can be known from the table 1 and the figure 5, the number density of the dispersed particles is 3 orders of magnitude worse than that of the example 1, and the invention again proves that the M1 element has indispensable effect in the alloy system of the invention;
the comparative example 2 is not added with M2 element, and the thermal cracking coefficient is slightly better than that of the comparative example 1, but is also obviously higher than that of the embodiment of the invention, and meanwhile, the thermal stability of the eutectic phase is reduced without adding M2, so that the performance after brazing is obviously reduced;
the copper content of comparative example 3 exceeds the reasonable interval of the system of the present invention, theoretically, the addition of Cu can naturally widen the effective feeding temperature interval, and it is clear from table 1 that, although most of the structural features thereof relatively meet the expected requirements, it is obvious from table 2 that too high Cu can cause the quasi-solid phase region to be obviously enlarged, increase the hot cracking tendency, increase the hot cracking coefficient by as high as 96, further cause the generation of casting cracks and shrinkage porosity, and also cause the reduction of the melting point, and other similar elements such as Mg, si, zn and the like can also produce similar effects;
comparative example 4 is free of copper, and practice shows that, as shown in fig. 6, the effective feeding temperature is extremely narrow, so that insufficient feeding is caused in the casting process, shrinkage cavities are formed, and the mechanical properties are negatively affected; as shown in table 1, the loss of copper also reduces precipitation of dispersed particles, and the reduction of dispersed particles further reduces the mechanical properties of the alloy, which can be verified in table 2, and the experimental results in table 2 show that the mechanical properties of the alloy without copper are obviously reduced, whether the alloy is in an as-cast state before brazing or in a mechanical state after brazing;
in conclusion, the A1-Mn-Fe-Cu-M1-M2 casting alloy provided by the invention has good casting performance, smaller hot cracking tendency, higher melting point, good brazeability and good mechanical property, and can meet the requirements of castings for high-temperature brazing in the field of new energy automobiles.
The above embodiments are provided to illustrate the technical concept and features of the present invention and are intended to enable those skilled in the art to understand the content of the present invention and implement the same, and are not intended to limit the scope of the present invention. All equivalent changes or modifications made in accordance with the spirit of the present invention should be construed to be included in the scope of the present invention.
The endpoints and any values of the ranges disclosed herein are not limited to the precise range or value, and are understood to encompass values approaching those ranges or values. For numerical ranges, one or more new numerical ranges may be found between the endpoints of each range, between the endpoint of each range and the individual point value, and between the individual point value, in combination with each other, and are to be considered as specifically disclosed herein.
Claims (19)
1. A cast aluminum alloy suitable for brazing, characterized in that the alloy structure of the cast aluminum alloy comprises an α -Al matrix and a eutectic structure;
wherein the size of the alpha-Al matrix is less than or equal to 150 mu m, and the secondary dendrite wall spacing is less than or equal to 30 mu m; and saidThe alpha-Al matrix can separate out dispersed particles with thermal stability in the brazing process, the size of the dispersed particles is 0.1-5 mu m, and the dispersed particles comprise Al 3 M1 particles, al 6 (Fe, mn, M2) particles, the number density of the dispersed particles being 10 6 ~10 10 Individual/cm 2 ；
The eutectic structure comprises alpha-Al phase and Al 6 (Fe, mn) phase, al 6 (Fe, mn, M2) phase and Al 6 (Fe, mn, cu, M2) phase, said Al 6 (Fe, mn) phase, the Al 6 (Fe, mn, M2) phase, the Al 6 The (Fe, mn, cu, M2) phase independently has a size of 1 to 50 μm;
the area of the eutectic structure accounts for 1/10-3/10 of the area of the alloy structure;
m1 is one or two selected from Ti and Zr, and M2 is one or more selected from V, mo and Cr;
the cast aluminum alloy comprises the following components in percentage by mass:
Mn 1.0~3.0%
Fe 0.1~1.0%
Cu 0.05~1.0%
M1 0.02~0.6%
M2 0.02~1.0%，
the balance being Al and unavoidable impurities.
2. The braze-suitable cast aluminum alloy of claim 1, wherein the Al 6 (Fe, mn) phase, the Al 6 (Fe, mn, M2) phase, the Al 6 The shape of the (Fe, mn, cu, M2) phase includes bulk, short fiber, and worm, respectively, independently.
3. The braze-suitable cast aluminum alloy of claim 2, wherein the Al 6 (Fe, mn) phase, the Al 6 (Fe, mn, M2) phase or said Al 6 In the (Fe, mn, cu, M2) phase, the eutectic phase with short fiber shape and worm shape accounts for more than 80 percent in total.
4. Adapted as claimed in claim 1A brazed cast aluminum alloy, characterized in that the dispersed particles further comprise Al 6 (Fe, mn) particles, al 6 One or two of (Fe, mn, cu, M2) particles.
5. The cast aluminum alloy suitable for brazing according to claim 1, wherein the composition of the cast aluminum alloy comprises impurity silicon, and the dispersed particles further comprise alpha-Al (Fe, mn, M2) Si particles and/or alpha-Al (Fe, mn, cu, M2) Si particles.
6. The cast aluminum alloy suitable for brazing according to claim 1, wherein the average size of the α -Al matrix is 20 to 120 μm and the average secondary dendrite wall spacing is 5 to 30 μm.
7. The cast aluminum alloy suitable for brazing according to claim 1, wherein the dispersed particles have an average size of 0.1-3 μm; and/or the number density of the dispersed particles is 10 7 ~10 10 Individual/cm 2 。
8. The cast aluminum alloy suitable for brazing according to claim 1, wherein the cast aluminum alloy comprises the following components in mass percent:
Mn 1.0~2.8%
Fe 0.1~1.0%
Cu 0.05~0.7%
M1 0.02~0.4%
M2 0.02~0.8%，
the balance being Al and unavoidable impurities.
9. The cast aluminum alloy suitable for brazing according to claim 1, wherein the content of the impurities in the cast aluminum alloy is controlled to be less than 0.2% in mass percent.
10. The cast aluminum alloy suitable for brazing as recited in claim 9, wherein the impurities comprise one or more of Mg, si, zn.
11. The cast aluminum alloy suitable for brazing as recited in claim 1, wherein the method of making the cast aluminum alloy comprises:
weighing the components according to the formula amount, and melting to obtain a melt;
adding a refining auxiliary agent into the melt, and refining to obtain a metal melt;
cooling the metal melt to obtain the cast aluminum alloy; wherein the cooling rate of the cooling is controlled to be more than or equal to 2 ℃/s.
12. The braze-suitable cast aluminum alloy of any of claims 1-11, wherein the cast aluminum alloy has a thermal cracking coefficient of less than 50.
13. The braze-suitable cast aluminum alloy of claim 12, wherein the cast aluminum alloy has a thermal cracking coefficient of 45 or less.
14. The cast aluminum alloy suitable for brazing according to any one of claims 1-11, wherein the cast aluminum alloy has a melting point of 600-650 ℃.
15. The cast aluminum alloy suitable for brazing according to any one of claims 1 to 11, wherein the cast aluminum alloy has a tensile strength of 145MPa or more, a yield strength of 75MPa or more, and an elongation of 12% or more at room temperature in an as-cast state.
16. The cast aluminum alloy suitable for brazing according to any one of claims 1 to 11, wherein after brazing, the cast aluminum alloy has a tensile strength of 140MPa or more, a yield strength of 70MPa or more, and an elongation of 12% or more at room temperature.
17. An aluminum alloy casting, characterized in that it is produced by melting and casting the cast aluminum alloy suitable for brazing as claimed in any one of claims 1 to 16, or by melting and refining the raw material components of the cast aluminum alloy suitable for brazing as claimed in any one of claims 1 to 16.
18. The metal product is characterized in that a metal melt is cast to obtain a casting, and the casting is welded with other metal materials in a brazing mode to prepare the metal product;
the metal melt is obtained by melting the cast aluminum alloy suitable for brazing according to any one of claims 1 to 16, or the metal melt is obtained by melt-refining the raw material components of the cast aluminum alloy suitable for brazing according to any one of claims 1 to 16;
and controlling the cooling rate to be more than or equal to 2 ℃/s in the casting process.
19. The metal article of claim 18, wherein the brazing has a welding temperature of 590-620 ℃.
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