CN114752828B - 5-series aluminum alloy plate for upper cover of automobile power battery pack and preparation method thereof - Google Patents
5-series aluminum alloy plate for upper cover of automobile power battery pack and preparation method thereof Download PDFInfo
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- H01M50/00—Constructional details or processes of manufacture of the non-active parts of electrochemical cells other than fuel cells, e.g. hybrid cells
- H01M50/20—Mountings; Secondary casings or frames; Racks, modules or packs; Suspension devices; Shock absorbers; Transport or carrying devices; Holders
- H01M50/249—Mountings; Secondary casings or frames; Racks, modules or packs; Suspension devices; Shock absorbers; Transport or carrying devices; Holders specially adapted for aircraft or vehicles, e.g. cars or trains
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- H01M50/20—Mountings; Secondary casings or frames; Racks, modules or packs; Suspension devices; Shock absorbers; Transport or carrying devices; Holders
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Abstract
The invention relates to a 5-series aluminum alloy plate for an upper cover of an automobile power battery pack and a preparation method thereof, and belongs to the technical field of aluminum alloy production. The composite material is prepared from the following element components in percentage by weight: si:0 to 0.10 percent of Fe:0 to 0.20 percent of Cu:0.15 to 0.25 percent of Mn:0.35 to 0.45 percent of Mg:4.50 to 5.00 percent of V:0.05 to 0.15 percent, single impurities less than or equal to 0.05 percent, total impurities less than or equal to 0.10 percent, and the balance of Al; wherein, alkali metal requires: na is less than or equal to 10ppm, ca is less than or equal to 8ppm, li is less than or equal to 15ppm, and the outstanding problem of the surface quality defect of TYPE B-TYPE Lv Des strip which is easy to appear in the application of the upper cover of the automobile power battery pack of the existing 5 aluminum alloy is solved through the process steps of casting, sawing, homogenizing, hot rolling, cold rolling and complete recrystallization annealing.
Description
Technical Field
The invention belongs to the technical field of aluminum alloy production, and particularly relates to a 5-series aluminum alloy plate for an upper cover of an automobile power battery pack and a preparation method thereof.
Background
Modern automobile technology is gradually developed towards energy conservation, environmental protection, safety and the like. The energy consumption of a vehicle is proportional to the total mass of the vehicle, and a lightweight design is an important subject in the development of automobile technology. For the pure electric passenger car, the whole car is light, so that the energy consumption and the environmental pollution are reduced, and meanwhile, the endurance mileage of the pure electric passenger car is obviously improved.
In 5000 series aluminum alloys, the interaction of dislocations with Mg atoms in solid solution is a major cause of unstable plastic deformation during unidirectional stretching. In alloys with Mg contents exceeding 2%, this unstable rheology appears in the form of an elongation at yield point, known as Lv De elongation. Such non-uniform deformation occurs after an initial small amount of strain by applying a constant stress; thereafter, a high strain is applied and the Dynamic Strain Aging (DSA) effect manifests itself as discontinuous or jagged yield. FIG. 1 is a stress-strain curve of a typical 5-series aluminum alloy; FIG. 2 is a stress-strain curve and TYPE A and TYPE B surface textures of aluminum alloy; it can be clearly seen that Lv De extends the plateau and the serrations or discontinuously yields, with the luer strips and serrations yielding during stretching causing the surface to exhibit TYPE a and TYPE B surface textures. Experience has shown that TYPE A-TYPE surface Lv-Des bands can be avoided by eliminating the yield plateau by uniaxial stretching, but TYPE B-TYPE surface Lv-Des bands are unavoidable.
For TYPE B ludes bands, this is mainly due to the phenomenon of plastic instability, i.e. stress fluctuations that appear as "saw-tooth" on the stress-strain curve, and the generation of repeatedly propagating local deformation bands on the sample, a phenomenon known as PLC effect. The most widely accepted theory of "dynamic strain aging" (Dynamic strain aging, DSA) is the cause of this phenomenon. The theory holds that movable dislocations, which act as line defects in the crystal, cause lattice wastage in the vicinity and thus stress fields, are hindered by obstructions in the crystal (e.g., forest dislocations, grain boundaries, etc.) during movement. Under the action of stress field, solute atoms are biased to the movable dislocation by diffusion mode to form solute atom air group ruthenium-binding movable dislocation. Under the action of the external stress field, the movable dislocation overcomes the obstacle in a thermal activation mode, and continues to move forwards after being free from pinning. This repeated pinning and de-pinning process between the mobile dislocations and solute atoms is manifested as a zigzag yield phenomenon on the macroscopic stress strain curve.
The existing 5XXX series aluminum alloy takes Mg as a main alloy element, and is a heat treatment-free reinforced alloy. Mg atoms are solid-dissolved in the aluminum matrix to form a solid-solution strengthening effect. The alloy has the strength, formability, corrosion resistance and welding performance similar to those of common carbon steel plates. The alloy strength is mainly determined by Mg content and strain strengthening degree, and is obtained by work hardening, and is generally used in O (annealed) state, and is generally used for complicated shape parts such as inner panels due to its excellent formability. Among the 5 series aluminum alloys, 5182-O and 5182-RSS are the most typical alloys, and are particularly suitable for parts formed by the extension method, such as a vehicle cover, a rear trunk lid, a load floor, an air filter, and the like. However, in the practical application, the complex shape of the alloy is more or less poor, and the obvious TYPE B-TYPE Lv Des strip and other problems exist on the surface after stamping, so that the large-scale popularization and application of 5000-series automobile plates are affected.
Disclosure of Invention
In view of the above, the invention aims to provide a 5-series aluminum alloy plate for an upper cover of an automobile power battery pack and a preparation method thereof, which solve the outstanding problem of surface quality defects of TYPE B-TYPE Ludbis strips easily occurring in the application of the upper cover of the automobile power battery pack of the existing 5-series aluminum alloy.
In order to achieve the above purpose, the present invention provides the following technical solution, including the following steps:
a5-series aluminum alloy plate for an upper cover of an automobile power battery pack is prepared from the following element components in percentage by weight: si:0 to 0.10 percent of Fe:0 to 0.20 percent of Cu:0.15 to 0.25 percent of Mn:0.35 to 0.45 percent of Mg:4.50 to 5.00 percent of V:0.05 to 0.15 percent, single impurities less than or equal to 0.05 percent, total impurities less than or equal to 0.10 percent, and the balance of Al; wherein, alkali metal requires: na is less than or equal to 10ppm, ca is less than or equal to 8ppm, and Li is less than or equal to 15ppm.
The preparation method of the 5-series aluminum alloy plate for the upper cover of the automobile power battery pack comprises the following steps of:
s1, casting: placing the prepared aluminum alloy raw materials into a heat preservation furnace with the temperature of 700-760 ℃, and starting electromagnetic stirring to melt; adjusting the temperature of the holding furnace to 720-740 ℃, and introducing Cl-Ar mixed gas for refining; then Al-Ti-B is introduced for refining; the aluminum alloy trapezoidal slab ingot is formed by casting after degassing and filtering;
s2, sawing and milling: sawing and milling all sides of an aluminum alloy trapezoidal flat ingot;
s3, homogenizing: homogenizing by adopting a heating furnace, firstly raising the temperature of the sawn and milled trapezoidal aluminum alloy slab ingot to 540 ℃, preserving heat for 6 hours, and then lowering the temperature to 500 ℃ and preserving heat for 2-12 hours;
s4, hot rolling: the homogenized aluminum alloy trapezoidal slab ingot enters a rough rolling process within 5min, rough rolling is carried out for 17-21 times, the thickness of an intermediate billet after rough rolling is 32mm, then 4 continuous finish rolling process is carried out, the total rolling reduction rate of finish rolling is more than 80%, the thickness of a final finish rolling coil billet is 4.5mm, the temperature of the coil billet is 310-330 ℃, and natural cooling is carried out;
s5, cold rolling: cold rolling the hot-rolled aluminum alloy plate to 1.2mm, and sequentially passing through 4.5mm, 2.3mm, 1.7mm and 1.2mm, wherein the cold rolling reduction rate is 80%;
s6, complete recrystallization annealing: carrying out complete recrystallization annealing on the cold-rolled aluminum alloy plate, firstly heating the aluminum alloy plate to 210 ℃, and preserving heat for 3 hours; then the aluminum alloy plate is continuously heated to 460 ℃ for 2 hours of heat preservation, then is cooled to 260 ℃ along with the furnace, and then is discharged from the furnace for air cooling.
Further, in the step S1, recycled aluminum, industrial pure Mg, industrial pure Zn, intermediate alloy Al-Si, intermediate alloy Al-Cu, intermediate alloy Al-Fe, intermediate alloy Al-Mn and/or intermediate alloy Al-V are adopted as the aluminum alloy raw material.
Further, in step S1, the aluminum alloy trapezoidal slab has a size of 630mm×190 mm×600 mm.
Further, in the step S2, at least 200mm of the leading end of the trapezoid aluminum alloy slab ingot is cut off, at least 100mm of the gate end is cut off, at least 10mm of the large-surface single face is milled, at least 5mm of the small-surface inclined face is milled, and at least 5mm of the small-surface vertical face is milled.
In step S3, a pusher gas heating furnace is used for homogenization treatment.
Further, in step S6, a box annealing furnace is used for the complete recrystallization annealing.
The invention has the beneficial effects that:
1. optimizing alloy composition
Cu element is added, and the content of the Cu element is 0.15-0.25%. Cu atoms in 5-series aluminum alloy as Al 2 Cu and Al 2 Shape of CuMg phaseThe formula (I) exists. Al is made by process control 2 Cu and Al 2 The CuMg phase exists in a dispersed form. The Mn element content is increased mainly because a small amount of Mn element exists in the alloy matrix in the form of solid solution in the alloy, and most of Mn forms Al with Al 6 Mn dispersed particles. The V element is added, and the V transition group metal element is added, so that dispersion aluminide particles can be generated, and dispersion strengthening effect is generated. V element is decomposed from saturated solid solution during as-cast homogenization and heat treatment to separate out dispersed VAl 11 Phase, dispersed vat 11 The phase is basically small particles of 0.5 μm or less, and once these particles are precipitated, it is difficult to continue dissolution and aggregation.
By adding alloy elements, a second phase which is dispersed and distributed is introduced into the 5-series aluminum alloy, and the repeated pinning and unpinning process between the second relatively movable dislocation and solute atoms which are dispersed and distributed causes interference, and the interference is mainly realized by the following two modes: firstly, the existence of the dispersed second phase has a great promotion effect on the proliferation of dislocation in the motion process of the movable dislocation, and the rapid proliferation of the dislocation leads the strength of the material to be continuously improved, which counteracts the softening phenomenon that the movable dislocation continues to move forwards after being free from pinning to a certain extent, and leads the sawtooth phenomenon of a stress strain curve to be weakened; 2. the propagation process of the second relatively movable dislocation distributed in a diffusion way under an external stress field generates a macroscopically uniform distributed blocking effect, so that the propagation of the movable dislocation is macroscopically more uniform, and the influence of DSA effect is counteracted to a certain extent.
2. And (5) carrying out finished product complete recrystallization annealing in a box-type annealing furnace.
Compared with a common box-type annealing furnace, the air cushion furnace can realize rapid temperature rise, has high temperature precision of the strip, good surface quality and uniform performance, but also has the problem of high production cost, and is not convenient for large-scale popularization and application of the aluminum alloy automobile plate.
The annealing and heating process of the air cushion furnace mainly applied to the current 5-series aluminum alloy automobile plate is too short in time, and can not effectively realize dispersion and precipitation of the second phase of the microalloy element, so as to promote a large amount of diffusion of the second phaseThe precipitation is realized, the expected purpose is realized, and after cold rolling, a box type annealing furnace is adopted to anneal the finished product, so that the long-term heating treatment at high temperature can realize Al 2 Cu、Al 2 CuMg、Al 6 And Mn and the like are fully dispersed and separated out.
Meanwhile, mn and V are typical fine-grain elements, so that the grain size after annealing can be kept within a reasonable range, and the uniformity of the whole coil grain size is also facilitated.
3. Aiming at the blank of the research on the TYPE B-TYPE Lv-Des strip after stamping in the prior patent, the invention comprehensively considers the aspects of corrosion, strength, stamping formability and the like, and develops and researches the outstanding problems of the surface quality defect and the like of the TYPE B-TYPE Lv-Des strip which are unavoidable in the application of the upper cover of the battery box of the prior 5-series aluminum alloy. By optimizing alloy components and improving original process routes and parameters, the surface quality of the aluminum alloy plate after stamping is obviously improved, and the aluminum alloy plate can be widely applied to 5-series aluminum alloy materials of automobile body inner plates, battery box upper covers, automobile bottom plates and other parts.
Additional advantages, objects, and features of the invention will be set forth in part in the description which follows and in part will become apparent to those having ordinary skill in the art upon examination of the following or may be learned from practice of the invention. The objects and other advantages of the invention may be realized and obtained by means of the instrumentalities and combinations particularly pointed out in the specification.
Drawings
For the purpose of making the objects, technical solutions and advantages of the present invention more apparent, the present invention will be described in the following preferred detail with reference to the accompanying drawings, in which:
FIG. 1 is a stress strain curve of a typical 5-series aluminum alloy
FIG. 2 is a stress-strain curve and TYPE A and TYPE B surface textures of a uniaxially stretched aluminum alloy;
FIG. 3 shows the surface quality of the aluminum alloy after stamping;
fig. 4 is a surface quality of the aluminum alloy after stamping.
Detailed Description
Other advantages and effects of the present invention will become apparent to those skilled in the art from the following disclosure, which describes the embodiments of the present invention with reference to specific examples. The invention may be practiced or carried out in other embodiments that depart from the specific details, and the details of the present description may be modified or varied from the spirit and scope of the present invention. It should be noted that the illustrations provided in the following embodiments merely illustrate the basic idea of the present invention by way of illustration, and the following embodiments and features in the embodiments may be combined with each other without conflict.
Examples
A5-series aluminum alloy plate for an upper cover of an automobile power battery pack is prepared from the following element components in percentage by weight: si:0 to 0.10 percent of Fe:0 to 0.20 percent of Cu:0.15 to 0.25 percent of Mn:0.35 to 0.45 percent of Mg:4.50 to 5.00 percent of V:0.05 to 0.15 percent, single impurities less than or equal to 0.05 percent, total impurities less than or equal to 0.10 percent, and the balance of Al; wherein, alkali metal requires: na is less than or equal to 10ppm, ca is less than or equal to 8ppm, and Li is less than or equal to 15ppm. And the element contents in table 1 are specifically adopted for proportioning.
And comprises the following steps:
s1, casting: the weight percentages of recycled aluminum, industrial pure Mg, industrial pure Zn, intermediate alloy Al-Si, intermediate alloy Al-Cu, intermediate alloy Al-Fe, intermediate alloy Al-Mn and/or intermediate alloy Al-V in the table 1 are adopted for proportioning; placing the prepared aluminum alloy raw materials into a heat preservation furnace with the temperature of 700-760 ℃, and starting electromagnetic stirring to melt; adjusting the temperature of the holding furnace to 720-740 ℃, and introducing Cl-Ar mixed gas for refining; then Al-Ti-B is introduced for refining; performing semi-continuous casting (DC casting) after degassing and filtering to form an aluminum alloy trapezoidal flat ingot; the aluminum alloy trapezoidal slab was sized 630mm x 190 mm x 600 mm.
S2, sawing and milling: sawing and milling all sides of an aluminum alloy trapezoidal flat ingot; at least 200mm of the leading end of the trapezoid aluminum alloy slab ingot, at least 100mm of the pouring gate end, at least 10mm of the large-surface single face and at least 5mm of the small-surface inclined face are cut, and at least 5mm of the small-surface vertical face is cut.
S3, homogenizing: homogenizing by adopting a push-type gas heating furnace, firstly raising the temperature of a sawn and milled trapezoidal aluminum alloy slab ingot to 540 ℃, preserving heat for 6 hours, and then reducing the temperature to 500 ℃ and preserving heat for 2-12 hours;
s4, hot rolling: the homogenized aluminum alloy trapezoidal slab ingot enters a rough rolling process within 5min, rough rolling is carried out for 17-21 times, the thickness of an intermediate billet after rough rolling is 32mm, then 4-connection finish rolling process is carried out, the total rolling reduction rate of finish rolling is more than 80%, the thickness of a final finish rolling coil billet is 4.5mm, the temperature of the coil billet is 310-330 ℃, and the coil billet is naturally cooled to room temperature;
s5, cold rolling: cold rolling the hot-rolled aluminum alloy plate to 1.2mm, and sequentially passing through 4.5mm, 2.3mm, 1.7mm and 1.2mm, wherein the cold rolling reduction rate is 80%;
s6, complete recrystallization annealing: carrying out complete recrystallization annealing on the cold-rolled aluminum alloy plate by adopting a box annealing furnace, firstly heating the aluminum alloy plate to 210 ℃, and preserving heat for 3 hours, wherein the process is an oil removal section process; then the aluminum alloy plate is continuously heated to 460 ℃ for 2 hours of heat preservation, then is cooled to 260 ℃ along with the furnace, and then is discharged from the furnace for air cooling.
Comparative example
Comparative examples the conventional AA5182 alloy compositions, specific elemental weight percentages as shown in table 1, were prepared in accordance with the examples for the casting, sawing, homogenization, hot rolling, and cold rolling process parameters in the specific process route, and were different from the examples in that: and (3) annealing the cold-rolled aluminum alloy plate by adopting a continuous air cushion furnace, wherein the heating rate is not more than 5 ℃/s, heating to 510 ℃ and preserving heat for 10s, and then carrying out forced air cooling, wherein the temperature of the aluminum alloy plate after air cooling is not more than 150 ℃.
Table 1 description of the weight percentages of the aluminum alloy elements of the examples and comparative examples
| Example of the other | Si | Fe | Cu | Mn | Mg | Cr | V |
| Examples | 0.08 | 0.16 | 0.22 | 0.39 | 4.56 | 0.03 | 0.12 |
| Comparative example | 0.07 | 0.15 | 0,02 | 0.15 | 4.59 | 0.03 | 0.00 |
The comparative examples and examples were subjected to mechanical tests and particle size comparisons, and the results are shown in tables 2 and 3;
table 2 comparative examples and results of comparative tests on mechanical properties
TABLE 3 comparison of grain size after annealing
| Example of the other | Head/. Mu.m | Middle part/. Mu.m | Tail/μm |
| Comparative example | 34 | 36 | 34 |
| Examples | 18 | 18 | 18 |
Aiming at the blank of the research on the TYPE B-TYPE Lv-Des strip after stamping in the prior patent, the invention comprehensively considers the aspects of corrosion, strength, stamping formability and the like, and develops and researches the outstanding problems of the surface quality defect and the like of the TYPE B-TYPE Lv-Des strip which are unavoidable in the application of the upper cover of the battery box of the prior 5-series aluminum alloy. From the tables 1-3 and the attached figures 3-4, it can be concluded that the invention obtains a novel 5-series alloy with obviously improved surface quality, excellent comprehensive performance, smooth and fine surface quality after stamping and obviously optimized TYPE B-TYPE Lv-Des strip by optimizing alloy components and improving original process route and parameters, and simultaneously obviously reduces manufacturing cost, can further expand application range of the aluminum alloy plate in the field of automobile light weight, can be widely applied to 5-series aluminum alloy materials of parts such as automobile body inner plates, battery box upper covers, automobile bottom plates and the like, and promotes development of new energy automobiles and light weight enterprises in China.
Finally, it is noted that the above embodiments are only for illustrating the technical solution of the present invention and not for limiting the same, and although the present invention has been described in detail with reference to the preferred embodiments, it should be understood by those skilled in the art that modifications and equivalents may be made thereto without departing from the spirit and scope of the present invention, which is intended to be covered by the claims of the present invention.
Claims (3)
1. The preparation method of the 5-series aluminum alloy plate for the upper cover of the automobile power battery pack comprises the following steps of: si: 0-0.10%, fe: 0-0.20%, cu: 0.15-0.25%, mn: 0.35-0.45%, mg: 4.50-5.00%, V: 0.05-0.15%, single impurities less than or equal to 0.05%, total impurities less than or equal to 0.10%, and the balance of Al; wherein, alkali metal requires: na is less than or equal to 10ppm, ca is less than or equal to 8ppm, and Li is less than or equal to 15ppm;
and comprises the following steps:
s1, casting: placing the prepared aluminum alloy raw materials into a heat preservation furnace with the temperature of 700-760 ℃, and starting electromagnetic stirring to melt; adjusting the temperature of the holding furnace to 720-740 ℃, and introducing Cl-Ar mixed gas for refining; then Al-Ti-B is introduced for refining; the aluminum alloy trapezoidal slab ingot is formed by casting after degassing and filtering; the aluminum alloy raw materials adopt recycled aluminum, industrial pure Mg, industrial pure Zn, intermediate alloy Al-Si, intermediate alloy Al-Cu, intermediate alloy Al-Fe, intermediate alloy Al-Mn and intermediate alloy Al-V;
s2, sawing and milling: sawing and milling all sides of an aluminum alloy trapezoidal flat ingot;
s3, homogenizing: homogenizing by adopting a pushing type gas heating furnace, firstly raising the temperature of a sawed and milled trapezoidal aluminum alloy slab ingot to 540 ℃, preserving heat for 6 hours, and then lowering the temperature to 500 ℃ and preserving heat for 2-12 hours;
s4, hot rolling: the homogenized aluminum alloy trapezoidal slab ingot enters a rough rolling process within 5min, rough rolling is carried out for 17-21 times, the thickness of an intermediate billet after rough rolling is 32mm, then 4-connection finish rolling process is carried out, the total rolling reduction rate of finish rolling is more than 80%, the thickness of a final finish rolling coil billet is 4.5mm, the temperature of the coil billet is 310-330 ℃, and natural cooling is carried out;
s5, cold rolling: cold rolling the hot-rolled aluminum alloy plate to 1.2mm, and sequentially passing through 4.5mm, 2.3mm, 1.7mm and 1.2mm;
s6, complete recrystallization annealing: carrying out complete recrystallization annealing on the cold-rolled aluminum alloy plate, firstly heating the aluminum alloy plate to 210 ℃, and preserving heat for 3 hours; then continuously heating the aluminum alloy plate to 460 ℃ for 2 hours, cooling to 260 ℃ along with a furnace, and discharging and air cooling;
in step S6, a box annealing furnace is adopted for complete recrystallization annealing.
2. The method for manufacturing a 5-series aluminum alloy plate for an automotive power battery pack cover according to claim 1, wherein in the step S1, the aluminum alloy trapezoidal slab ingot has a size of 630mm x 190 mm x 600 mm.
3. The method for manufacturing a 5-series aluminum alloy plate for an upper cover of an automobile power battery pack according to claim 1, wherein in the step S2, the leading end of the trapezoid aluminum alloy slab ingot is cut off by at least 200mm, the pouring gate end is cut off by at least 100mm, the large-surface single face is milled by at least 10mm, the small-surface inclined face is milled by at least 5mm, and the small-surface vertical face is milled by at least 5mm.
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