CN106011847A - In-situ non-crystallizing modification method for surface of metal material - Google Patents
In-situ non-crystallizing modification method for surface of metal material Download PDFInfo
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- CN106011847A CN106011847A CN201610583224.9A CN201610583224A CN106011847A CN 106011847 A CN106011847 A CN 106011847A CN 201610583224 A CN201610583224 A CN 201610583224A CN 106011847 A CN106011847 A CN 106011847A
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C24/00—Coating starting from inorganic powder
- C23C24/08—Coating starting from inorganic powder by application of heat or pressure and heat
- C23C24/10—Coating starting from inorganic powder by application of heat or pressure and heat with intermediate formation of a liquid phase in the layer
- C23C24/103—Coating with metallic material, i.e. metals or metal alloys, optionally comprising hard particles, e.g. oxides, carbides or nitrides
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C24/00—Coating starting from inorganic powder
- C23C24/08—Coating starting from inorganic powder by application of heat or pressure and heat
- C23C24/10—Coating starting from inorganic powder by application of heat or pressure and heat with intermediate formation of a liquid phase in the layer
- C23C24/103—Coating with metallic material, i.e. metals or metal alloys, optionally comprising hard particles, e.g. oxides, carbides or nitrides
- C23C24/106—Coating with metal alloys or metal elements only
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- Mechanical Engineering (AREA)
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- Organic Chemistry (AREA)
- Laser Beam Processing (AREA)
- Powder Metallurgy (AREA)
- Other Surface Treatments For Metallic Materials (AREA)
Abstract
The invention belongs to the technical field of modification of surfaces of metal materials, and discloses an in-situ non-crystallizing modification method for the surface of a metal material. The method comprises the steps that amorphous alloy components matched with components of a metal matrix material are selected based on the components of the metal matrix material; then, required simple-substance element powder except main elements of a metal matrix is matched according to the amorphous alloy components; after being mixed, the element powder is preplaced on the surface of the metal matrix; laser is adopted to directly irradiate the mixed powder and the metal matrix to melt the mixed powder and the metal matrix and mix the melts; and an amorphous alloy is generated through the in-situ alloying reaction of the mixed element powder and the main elements of the metal matrix under the condition of quick cooling, and an amorphous alloy surface is prepared. According to the method, the interfacial stress of the amorphous alloy surface and the metal matrix is effectively reduced, the thickness of the amorphous alloy surface is increased, and the surface performance of the metal material is remarkably improved; and the amorphous alloy surface prepared through the method is different from an amorphous alloy coating prepared through a traditional method, the amorphous alloy surface is generated through the in-situ alloying reaction on the surface of the metal matrix, the interface bonding is high, and the performance is excellent.
Description
Technical field
The invention belongs to technical field of metal material surface modification, be specifically related to a kind of metal material surface decrystallized modification side in situ
Method.
Background technology
Surface failure is the common form that key metal parts occur to destroy, therefore, and the service life of parts and its superficiality
Can be closely related.Surface modification is to improve the important means of metal material surface characteristics, it is possible to increase metal material surface opposing carries
The ability of lotus effect, the generation of suppression surface failure, increase the service life.Laser Surface Treatment is important process for modifying surface
One of, it is widely used to every field, it is achieved the surface peening of metallic element.
Non-crystaline amorphous metal has the atomic arrangement structure of longrange disorder and shortrange order, present high intensity, high rigidity, high resiliency should
The physicochemical properties that pole-changing limit, abrasion resistant and corrosion resistant etc. are excellent so that it is be highly suitable to be applied for the surface modification of metal material.Swash
Light upper shaft, also known as lam, is to utilize high energy laser beam direct irradiation metal surface quickly to add heat fusing and cooled and solidified and obtain
To the method for surface amorphous layers, it is remarkably improved the mechanics on metal or alloy top layer, physics and chemical property, but the party's legal system
The thinner thickness of standby amorphous layer, and its application limited by alloying component.Amorphous coating preparation is another kind of metal surface amorphous
Change technology, conventional method has thermal spraying, chemical plating, magnetron sputtering and laser melting coating etc..The technical process of first three methods is relatively
Complexity, the amorphous coating of preparation is relatively thin, and its application scenario is severely limited.Laser melting coating is to utilize high energy laser beam irradiation to melt
Cover material and be thermally formed molten bath with matrix skin with the firing rate being exceedingly fast, then quickly coagulating from Quench by cladding material melt
Admittedly prepare amorphous coating, and form metallurgical binding with matrix skin.Although the method can prepare thicker amorphous coating, but it is relatively
Difficult obtain completely amorphous coating, and the interface cohesion of coating and matrix is difficult to control to.
The problem existed for existing method, the present invention, from preparation technology, proposes a kind of metal material surface the most decrystallized
Method of modifying.Technology immediate with the present invention is laser glazing and laser melting coating amorphous coating, but in preparation technology and principle
The present invention is that essence is different from both approaches, and the shortcoming that the present invention can effectively overcome both approaches.The present invention
Being the creative invention carrying out prior art, technical process is simple, easily operates, is suitable for large-scale batch production.Therefore,
High performance non-crystaline amorphous metal top layer can be prepared by the present invention, extend the service life of key components and parts, meet reality application
Demand.
Summary of the invention
It is an object of the invention to provide a kind of metal material surface decrystallized method of modifying in situ for the problems referred to above, the method is base
Composition in metal matrix material chooses matched amorphous alloy component, then according to amorphous alloy component proportioning except metal
The outer required simple substance element powders of matrix host element, is preset in metal base surface, uses laser direct irradiation mixed powder after mixing
End and metallic matrix make it melt-blended, are reacted by the home position alloying of mixed-powder element with metallic matrix host element and quick
Cooling condition generates non-crystaline amorphous metal, thus prepares non-crystaline amorphous metal top layer, significantly improves metal material surface characteristics, promotes its engineering
Application.
The technical scheme is that a kind of metal material surface decrystallized method of modifying in situ, based on metal matrix material with non-
The coupling system of peritectic alloy composition, uses laser in-situ amorphous method to prepare non-crystaline amorphous metal top layer at metal base surface, including
Following steps:
S1, metal material surface sand papering is polished, and use alcohol washes surface；
S2, select the system of mating of metal material and amorphous alloy component, and remove metal material master according to amorphous alloy component proportioning
Simple substance element powders outside element；
S3, the element powders prepared is carried out mechanical mixture, prepare uniform mixed-powder；
S4, mixed-powder is preset in metal material surface；
S5, the metal material of the employing preset mixed-powder of laser scanning, make mixed-powder and metal material top layer melt-blended concurrently
Raw non-crystaline amorphous metalization reaction, prepares non-crystaline amorphous metal top layer.
Preferably, the metal material of described step S1 be aluminum and aluminium alloy, magnesium and magnesium alloy, copper and copper alloy, titanium or titanium alloy,
Any one in nickel and nickel alloy or steel and cast iron.
Preferably, the system of mating of the metal material of described step S2 and amorphous alloy component is aluminum and aluminium alloy closes with aluminium-based amorphous alloy
Coupling system, magnesium and magnesium alloy and the magnesium base amorphous alloy of gold mate mating of system, copper and copper alloy and cu-based amorphous alloys
System, titanium or titanium alloy and titanium-based amorphous alloy mate system, nickel and nickel alloy and ni-based amorphous alloy mate system or
Person's steel and cast iron and Fe-based amorphous alloy mate in system any one.
Preferably, the average particulate diameter of the simple substance element powders of described step S2 is 10nm～100 μm.
Preferably, the mixed-powder of described step S3 be by the non-crystaline amorphous metal matched with metal material comprise except metal material master
The simple substance element powders of other elements outside element is constituted.
Preferably, the laser in described step S5 uses continuous CO2Or Nd:YAG laser instrument, peak power is respectively 5KW
And 2KW.
Further, the laser power using laser instrument is 0.5～3kW, and scanning speed is 10～100mm/s, and overlapping rate is
20～80%, protective gas is argon.
Beneficial effects of the present invention:
(1) amorphous alloy component selected by the present invention matches with metal matrix material, can effectively reduce non-crystaline amorphous metal top layer and gold
Belong to the interfacial stress of matrix.
(2) laser in-situ of the present invention decrystallized be by preset mixed-powder and the home position alloying of metallic matrix react generation non-
Peritectic alloy top layer, it is possible to be effectively increased the thickness on non-crystaline amorphous metal top layer, meets practical application request, further expansive approach scope.
(3) the non-crystaline amorphous metal top layer that prepared by the present invention is different from amorphous alloy coating prepared by traditional method, and non-crystaline amorphous metal top layer is
Generating in the most decrystallized reaction of metal base surface, interface cohesion is strong, excellent performance；And amorphous alloy coating is at metal
Basic surface transplants one layer of coating, relate to coating be combined with basal body interface, the challenge such as interface dilution rate, interface is difficult to control to,
It is unfavorable for the performance of non-crystaline amorphous metal self performance.
(4) laser in-situ amorphous method wide accommodation, technical process is simple, easily operates, and is suitable for extensive batch metaplasia
Produce.
Detailed description of the invention
Below in conjunction with specific embodiment, the present invention is further illustrated, but protection scope of the present invention is not limited to this.
Embodiment 1:
S1, by 45 steel sand for surface paper sanding and polishings, and use alcohol washes surface；
S2, select 45 steel and Fe42.5Cr16Mo16.5B9C16The coupling system of non-crystaline amorphous metal, and according to Fe42.5Cr16Mo16.5B9C16
Amorphous alloy component proportioning Cr, Mo, B and C simple substance element powders in addition to 45 steel host element Fe, the average grain of powder
Diameter is respectively 30 μm, 100 μm, 15 μm and 10 μm；
S3, Cr, Mo, B and C simple substance element powders prepared is carried out mechanical mixture, prepare uniform mixed-powder；
S4, mixed-powder is preset in 45 steel surfaces；
S5, use continuous CO245 steel of the preset mixed-powder of laser scanning, laser power is 1.5kW, and scanning speed is 50mm/s,
Overlapping rate is 20%, and protective gas is argon, makes mixed-powder and 45 steel top layers are melt-blended and occur non-crystaline amorphous metalization to react,
Prepare non-crystaline amorphous metal top layer.
Using microhardness testers to measure the hardness of the most decrystallized rear sample before modified, result shows, the most decrystallized rear sample
Microhardness is approximately 2.2 times of metal matrix material, it is seen then that after using the present invention to process, the hardness of metal material is significantly carried
High.Therefore the present invention is used can to prepare high performance noncrystalline surface in situ.
Embodiment 2:
S1, the sand papering of AZ91D Mg alloy surface is polished, and use alcohol washes surface；
S2, selection AZ91D magnesium alloy and Mg86.5Ni7.5Y6The coupling system of non-crystaline amorphous metal, and according to Mg86.5Ni7.5Y6Amorphous
The alloying component proportioning Ni and Y simple substance element powders in addition to AZ91D magnesium alloy host element Mg, the average particulate diameter of powder
It is respectively 15 μm and 75 μm；
S3, Ni and the Y simple substance element powders prepared is carried out mechanical mixture, prepare uniform mixed-powder；
S4, mixed-powder is preset in AZ91D Mg alloy surface；
S5, employing continuous Nd: YAG laser scans the AZ91D magnesium alloy of preset mixed-powder, and laser power is 0.5kW,
Scanning speed is 10mm/s, and overlapping rate is 30%, and protective gas is argon, makes mixed-powder melt with AZ91D magnesium alloy top layer
Change hybrid concurrency raw non-crystaline amorphous metalization reaction, prepare non-crystaline amorphous metal top layer.
Using microhardness testers to measure the hardness of the most decrystallized rear sample before modified, result shows, the most decrystallized rear sample
Microhardness is approximately 2.5 times of metal matrix material, it is seen then that after using the present invention to process, the hardness of metal material is significantly carried
High.Therefore the present invention is used can to prepare high performance original position noncrystalline surface.
Embodiment 3:
S1, the sand papering of Monel400 nickel alloy surfaces is polished, and use alcohol washes surface；
S2, selection Monel400 nickel alloy and Ni58Ti15Zr18Si3Sn2Nb4The coupling system of non-crystaline amorphous metal, and according to
Ni58Ti15Zr18Si3Sn2Nb4Amorphous alloy component proportioning Ti, Zr, Si, Sn in addition to Monel400 nickel alloy host element Ni and
Nb simple substance element powders, the average particulate diameter of powder is respectively 30 μm, 65 μm, 50nm, 10 μm and 48 μm；
S3, Ti, Zr, Si, Sn and Nb simple substance element powders prepared is carried out mechanical mixture, prepare uniform mixed-powder；
S4, mixed-powder is preset in Monel400 nickel alloy surfaces；
S5, use continuous CO2The Monel400 nickel alloy of the preset mixed-powder of laser scanning, laser power is 3kW, scanning
Speed is 100mm/s, and overlapping rate is 50%, and protective gas is argon, makes mixed-powder melt with Monel400 nickel alloy top layer
Change hybrid concurrency raw non-crystaline amorphous metalization reaction, prepare non-crystaline amorphous metal top layer.
Using microhardness testers to measure the hardness of the most decrystallized rear sample before modified, result shows, the most decrystallized rear sample
Microhardness is approximately 5.1 times of metal matrix material, it is seen then that after using the present invention to process, the hardness of metal material is significantly carried
High.Therefore the present invention is used can to prepare high performance original position noncrystalline surface.
Embodiment 4:
S1, the sand papering of H68 brass surfaces is polished, and use alcohol washes surface；
S2, selection H68 pyrite and Cu60Zr30Al10The coupling system of non-crystaline amorphous metal, and according to Cu60Zr30Al10Non-crystaline amorphous metal becomes
The distribution ratio Zr and Al simple substance element powders in addition to H68 pyrite host element Cu, the average particulate diameter of powder is respectively 50 μm
And 10nm；
S3, Zr and the Al simple substance element powders prepared is carried out mechanical mixture, prepare uniform mixed-powder；
S4, mixed-powder is preset in H68 brass surfaces；
S5, employing continuous Nd: YAG laser scans the H68 pyrite of preset mixed-powder, and laser power is 1kW, scanning speed
Degree is 30mm/s, and overlapping rate is 80%, and protective gas is argon, makes mixed-powder and H68 pyrite top layer melt-blended concurrently
Raw non-crystaline amorphous metalization reaction, prepares non-crystaline amorphous metal top layer.
Using microhardness testers to measure the hardness of the most decrystallized rear sample before modified, result shows, the most decrystallized rear sample
Microhardness is approximately 3 times of metal matrix material, it is seen then that after using the present invention to process, the hardness of metal material is significantly improved.
Therefore the present invention is used can to prepare high performance original position noncrystalline surface.
It is to be understood that, although this specification describes according to each embodiment, but the most each embodiment only comprises an independence
Technical scheme, this narrating mode of description be only the most for clarity sake, those skilled in the art should using description as
One entirety, the technical scheme in each embodiment can also through appropriately combined, formed it will be appreciated by those skilled in the art that other
Embodiment.
The a series of detailed description of those listed above is only for illustrating of the possible embodiments of the present invention, and they are also
Being not used to limit the scope of the invention, all Equivalent embodiments or changes made without departing from skill of the present invention spirit all should comprise
Within protection scope of the present invention.
Claims (7)
1. a metal material surface decrystallized method of modifying in situ, it is characterised in that based on metal matrix material and non-crystaline amorphous metal
The coupling system of composition, uses laser in-situ amorphous method to prepare non-crystaline amorphous metal top layer at metal base surface, including following step
Rapid:
S1, by metal material surface sanding and polishing, and clean surface；
S2, select the system of mating of metal material and amorphous alloy component, and remove metal material master according to amorphous alloy component proportioning
Simple substance element powders outside element；
S3, the element powders prepared is carried out mechanical mixture, prepare uniform mixed-powder；
S4, mixed-powder is preset in metal material surface；
S5, the metal material of the employing preset mixed-powder of laser scanning, make mixed-powder and metal material top layer melt-blended concurrently
Raw non-crystaline amorphous metalization reaction, prepares non-crystaline amorphous metal top layer.
Metal material surface the most according to claim 1 decrystallized method of modifying in situ, it is characterised in that described step
The metal material of S1 is aluminum and aluminium alloy, magnesium and magnesium alloy, copper and copper alloy, titanium or titanium alloy, nickel and nickel alloy or steel
And any one in cast iron.
Metal material surface the most according to claim 1 decrystallized method of modifying in situ, it is characterised in that described step
The metal material of S2 and amorphous alloy component mate system be aluminum and aluminium alloy with al based amorphous alloy mate system, magnesium and magnesium
Alloy and magnesium base amorphous alloy mate system, copper and copper alloy and cu-based amorphous alloys mate system, titanium or titanium alloy and titanium
Coupling system, nickel and the nickel alloy of base noncrystal alloy mates system or steel and cast iron with Fe-based amorphous with ni-based amorphous alloy
Any one in the coupling system of alloy.
Metal material surface the most according to claim 1 decrystallized method of modifying in situ, it is characterised in that described step
The average particulate diameter of the simple substance element powders of S2 is 10nm～100 μm.
Metal material surface the most according to claim 1 decrystallized method of modifying in situ, it is characterised in that described step
The mixed-powder of S3 is the simple substance element powder in addition to metal material host element comprised by the non-crystaline amorphous metal matched with metal material
End is constituted.
Metal material surface the most according to claim 1 decrystallized method of modifying in situ, it is characterised in that described step
Laser in S5 uses continuous CO2Or Nd:YAG laser instrument.
Metal material surface the most according to claim 6 decrystallized method of modifying in situ, it is characterised in that use laser instrument
Laser power be 0.5～3kW, scanning speed is 10～100mm/s, and overlapping rate is 20～80%, and protective gas is argon.
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Cited By (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108385103A (en) * | 2018-03-19 | 2018-08-10 | 南昌大学 | A kind of Magnesiumalloy surface modifying method based on electric-resistance seam-welding |
| CN108546893A (en) * | 2018-05-17 | 2018-09-18 | 吉林大学 | The method that laser irradiation promotes zirconium base or titanium-based amorphous alloy case hardness in nitrogen |
| CN109266980A (en) * | 2018-11-05 | 2019-01-25 | 淮阴工学院 | In the method that Mg alloy surface prepares bulk material amorphous layer |
| CN109957801A (en) * | 2017-12-25 | 2019-07-02 | 财团法人金属工业研究发展中心 | Surface modification method and products thereof |
| CN110396690A (en) * | 2019-08-08 | 2019-11-01 | 湘潭大学 | A kind of nickel-aluminum bronze surface laser cladding amorphous composite coating and preparation method thereof |
| CN111575542A (en) * | 2020-05-03 | 2020-08-25 | 上海工程技术大学 | Amorphous reinforced aluminum alloy composite material and preparation method thereof |
| CN111979539A (en) * | 2020-07-07 | 2020-11-24 | 燕山大学 | Copper-based amorphous composite coating and preparation method thereof |
| CN112195474A (en) * | 2020-10-14 | 2021-01-08 | 上海新能量纳米科技股份有限公司 | Metal surface modification process and application thereof |
| US11091831B1 (en) | 2020-02-04 | 2021-08-17 | Hamilton Sundstrand Corporation | Pulsed directed energy deposition based fabrication of hybrid titanium/aluminum material for enhanced corrosion resistance and strength |
| US11214002B2 (en) * | 2019-10-18 | 2022-01-04 | Hamilton Sundstrand Corporation | Additively manufacturing of amorphous structures |
| CN115141993A (en) * | 2021-09-08 | 2022-10-04 | 武汉苏泊尔炊具有限公司 | Method for manufacturing cookware |
| CN115181878A (en) * | 2022-09-14 | 2022-10-14 | 苏州慧金新材料科技有限公司 | Integrated die casting aluminum alloy for new energy automobile, and preparation method and application thereof |
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| CN103540790A (en) * | 2013-10-28 | 2014-01-29 | 北京工业大学 | Preparation method of corrosion-resistant CuAlCr laser cladding material |
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| CN103540790A (en) * | 2013-10-28 | 2014-01-29 | 北京工业大学 | Preparation method of corrosion-resistant CuAlCr laser cladding material |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN109957801A (en) * | 2017-12-25 | 2019-07-02 | 财团法人金属工业研究发展中心 | Surface modification method and products thereof |
| CN108385103A (en) * | 2018-03-19 | 2018-08-10 | 南昌大学 | A kind of Magnesiumalloy surface modifying method based on electric-resistance seam-welding |
| CN108546893A (en) * | 2018-05-17 | 2018-09-18 | 吉林大学 | The method that laser irradiation promotes zirconium base or titanium-based amorphous alloy case hardness in nitrogen |
| CN109266980A (en) * | 2018-11-05 | 2019-01-25 | 淮阴工学院 | In the method that Mg alloy surface prepares bulk material amorphous layer |
| CN110396690A (en) * | 2019-08-08 | 2019-11-01 | 湘潭大学 | A kind of nickel-aluminum bronze surface laser cladding amorphous composite coating and preparation method thereof |
| US11701821B2 (en) | 2019-10-18 | 2023-07-18 | Hamilton Sundstrand Corporation | Additively manufacturing of amorphous structures |
| US11214002B2 (en) * | 2019-10-18 | 2022-01-04 | Hamilton Sundstrand Corporation | Additively manufacturing of amorphous structures |
| US11091831B1 (en) | 2020-02-04 | 2021-08-17 | Hamilton Sundstrand Corporation | Pulsed directed energy deposition based fabrication of hybrid titanium/aluminum material for enhanced corrosion resistance and strength |
| US20210340667A1 (en) * | 2020-02-04 | 2021-11-04 | Hamilton Sundstrand Corporation | Pulsed directed energy deposition based fabrication of hybrid titanium/aluminum material for enhanced corrosion resistance and strength |
| CN111575542B (en) * | 2020-05-03 | 2021-04-06 | 上海工程技术大学 | Amorphous reinforced aluminum alloy composite material and preparation method thereof |
| CN111575542A (en) * | 2020-05-03 | 2020-08-25 | 上海工程技术大学 | Amorphous reinforced aluminum alloy composite material and preparation method thereof |
| CN111979539A (en) * | 2020-07-07 | 2020-11-24 | 燕山大学 | Copper-based amorphous composite coating and preparation method thereof |
| CN112195474A (en) * | 2020-10-14 | 2021-01-08 | 上海新能量纳米科技股份有限公司 | Metal surface modification process and application thereof |
| CN112195474B (en) * | 2020-10-14 | 2022-11-11 | 上海新能量纳米科技股份有限公司 | Metal surface modification process and application thereof |
| CN115141993A (en) * | 2021-09-08 | 2022-10-04 | 武汉苏泊尔炊具有限公司 | Method for manufacturing cookware |
| CN115181878A (en) * | 2022-09-14 | 2022-10-14 | 苏州慧金新材料科技有限公司 | Integrated die casting aluminum alloy for new energy automobile, and preparation method and application thereof |
| CN115181878B (en) * | 2022-09-14 | 2022-12-23 | 苏州慧金新材料科技有限公司 | Integrated die casting aluminum alloy for new energy automobile, and preparation method and application thereof |
| US11781202B1 (en) | 2022-09-14 | 2023-10-10 | Suzhou Huijin Smart Materials Technology Co., Ltd. | Aluminum alloy for new energy vehicle integral die-cast part, preparation method therefor and application thereof |
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| CN106011847B (en) | 2019-02-05 |
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