CN101474745B - Method for preparing AZ31B magnesium alloy pressing sheet material - Google Patents
Method for preparing AZ31B magnesium alloy pressing sheet material Download PDFInfo
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- CN101474745B CN101474745B CN2009100641122A CN200910064112A CN101474745B CN 101474745 B CN101474745 B CN 101474745B CN 2009100641122 A CN2009100641122 A CN 2009100641122A CN 200910064112 A CN200910064112 A CN 200910064112A CN 101474745 B CN101474745 B CN 101474745B
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Abstract
The present invention discloses a method for preparing AZ31B magnesium alloy pressing-formed plate, wherein the method is realized through the following steps: 1. preparing pressing-formed plate: adapting AZ31B magnesium alloy flat section ingot for executing homogenization treatment in a box-type electric resistance furnace, keeping the processing temperature of 420-450 DEG C for 18 hours; 2. rolling the board which comprises the following procedures: preparing the flat section ingot, milling surface, grinding, heating, hot rolling, cold rolling, annealing, performance detecting and obtainingthe finished product. The rolling start temperature of hot rolling is 450-460 DEG C. The deformation of hot rolling pass is 15-20%. The temperature of final rolling is 300+/-10 DEG C. The heating temperature is 430-450 DEG C. The heat preservation time is 1-1.5 hours until the thickness of board is 1-2mm. The deformation of cold rolling pass is about 5%. The deformation of total cold rolling is controlled below 25%. The thickness of finished board is 1.0-1.5mm. The recrystallization annealing is executed at a temperature of 260-300 DEG C. The heat preservation time is controlled to 60-90 minutes. The board prepared by the method has the advantages of good forming property under room temperature, no easy cracking in cold punching, high finished product rate. The board can be used for thin-wall products of mobile phone, television, computer casing, etc. which are manufactured by pressing-forming.
Description
Technical field
The invention belongs to the sheet material preparing technical field, be specifically related to the magnesium alloy punched sheet material preparation method of a kind of AZ31B.
Background technology
A series of premium properties such as magnesium alloy has light weight, specific stiffness, specific strength height, electromagnetic wave shielding is good and recycling is easy at home and abroad have been subjected to paying attention to widely, are regarded as the green metal material of 21 century.As the material lighter than aluminium, magnesium is far from bringing into play its due use value, and huge development potentiality is arranged.Magnesium alloy plate is mainly used in Aero-Space and military field at present, and the former Soviet Union, Germany and American Studies be morning, and effect is comparatively remarkable, mainly based on cut deal.Along with the rise of 3C Products such as auto industry, computer, instrument and meter, adapt to development trends such as lightness, portability, the demand of magnesium alloy increases suddenly.Worldwide start with output, the quality that improves magnesium alloy plate, the research boom that improves performance.About magnesium alloy plate punch forming process technology, domesticly also do not carry out system research, also just carried out a spot of research abroad.People such as Sugamata have tested the AEG-process of AZ31B magnesium alloy, find that at room temperature magnesium alloy has lower deep-draw ratio and Erichen value, along with the rising of temperature, and the also corresponding raising of these two parameters.In the time of 110 ℃, maximum deep-draw ratio is 1.67, and temperature is elevated to 180 ℃, and maximum deep-draw ratio can bring up to 2.2.Researchs such as K.Droder think that in the time of 200 to 250 ℃ the deep-draw ratio of AZ13B magnesium alloy can reach 2.52, can realize the punch forming of magnesium alloy, makes the magnesium alloy plate stamping parts become possibility in industrial application.The forming limit of AZ31B sheet material has been studied by the old rich nations of Taiwan's scholars etc., forming properties such as CCV value, but only limit to the research of forming property, the not report of formed product.German scholar E.Doege etc. have studied the thennoforming performance of AZ31B sheet material.In the time of 200～250 ℃, limiting drawing ratio β max=2.52.Point out simultaneously, during the magnesium alloy plate punching press, must heat, and provided the punching press photo of simulation part mould.The texture and the anisotropy of magnesium alloy plate studied by University Of Chongqing, and rolling magnesium alloy plate texture mainly is that basal plane texture is main plate texture.After cold rolling, basal plane tilts to rolling direction, make this direction plasticity be improved significantly.In electronics industry, adopt mobile phone, TV, the computer casing of the production of magnesium alloy plate stamping technology to compare with corresponding die casting product, there is wall to approach advantages such as reaching the productivity ratio height.Therefore magnesium alloy stamping part has a good application prospect, and exploitation magnesium alloy plate punching press and correlation technique thereof have important significance for theories and social benefit.But, because the magnesium alloy crystal structure is close-packed hexagonal (Hcp), plasticity is relatively poor, difficulty is shaped, lumber recovery is low, the wrong understanding of shortcoming such as people are inflammable to magnesium alloy, not corrosion-resistant in addition causes the punching press of wrought magnesium alloy sheet material not obtain large-scale application, and wrought magnesium alloy and Research on forming are also very insufficient.The sheet material of wrought magnesium alloy, section bar and forging are mainly used in fields such as Aeronautics and Astronautics and military affairs, do not spread to civil area.Economizing on resources and reducing under the social desirability of pollution, wrought magnesium alloy is beneficial to the STRATEGIES OF SUSTAINABLE DEVELOPMENT requirement, is badly in need of transition of people's conceptions, accelerates research, promotes its application in civil area.
The problem that present magnesium alloy punched sheet material need solve when rolling:
(1) magnesium alloy has close-packed hexagonal structure, when being lower than 225 ℃, plastic deformation be limited to basal plane 0001}＜1120〉slippage and the conical surface 1012}＜1011〉twin.Its low-temperature deformation has only three how much slip systems and two independent slip systems.Therefore the cold rolling poor performance of magnesium alloy is easy to crack.
(2) Chang Gui magnesium alloy punched sheet material cracking, fold often appear in punching course easily, phenomenon such as cave in, cause product rejection.These Sheet Metal Forming Technology factors are more, and situation is comparatively complicated, needs further investigation.
Summary of the invention
For solving the above-mentioned defective that prior art exists, the object of the present invention is to provide a kind of processability at room temperature good, not easy to crack during cold punching, the magnesium alloy punched sheet material preparation method of the AZ31B that yield rate is high.
For achieving the above object, the technical solution used in the present invention is that the magnesium alloy punched sheet material preparation method of this AZ31B follows these steps to realize: 1, pressing sheet material preparation: adopt AZ31B magnesium alloy slab ingot, slab ingot carries out homogenising in chamber type electric resistance furnace handles, treatment temperature is 420～450 ℃, is incubated 18 hours; 2, plate rolling: the rolling mill practice flow process of sheet material is: slab ingot → mill face → reconditioning → heating → hot rolling → cold rolling → annealing → Performance Detection → finished product, wherein the start rolling temperature of (1) hot rolling is 450～460 ℃, the hot rolling pass deflection is 15～20%, finishing temperature is 300 ± 10 ℃, heating-up temperature is 430～450 ℃, temperature retention time is 1～1.5 hour, carries out repeatedly, and be 1～2mm until sheet metal thickness; (2) cold rolling employing multi-pass small deformation amount is rolling, and pass deformation is about 5%, and total cold rolling reduction is controlled at below 25%, and the thickness of finished product sheet material is 1.0～1.5mm; (3) annealing process: carry out recrystallization annealing at 260～300 ℃, temperature retention time was controlled at 60～90 minutes.
Adopt the beneficial effect of technique scheme: the AZ31B magnesium alloy deformation mainly is two kinds of forms such as twin, slippage.Deformation temperature is during less than 300 ℃, twinly plays a part necessarily in plastic deformation, and along with temperature raises, the proportion of slippage increases, and provides the forming core condition for dynamic recrystallization.In 250～450 ℃ of deformation temperature scopes, dynamic recrystallization all can take place in magnesium alloy deformation.In view of the above, the best deformation temperature of magnesium alloy is 300～350 ℃ of scopes, and resistance of deformation is low, and plasticity is good, is easy to be shaped.The AZ31B magnesium alloy forms local dynamic recrystallized structure-" necklace " shape tissue when middle warm deformation, along with deformation temperature improves, " necklace " shape is organized less gradually or disappeared.When being out of shape under higher temperature, dynamic recrystallized structure is even.When deformation temperature was higher than 450 ℃, the crystal grain after the distortion was obviously grown up.Handle so AZ31B magnesium alloy slab ingot is carried out homogenising, eliminate component segregation, guarantee even tissue, improved the forming property of magnesium alloy slab ingot, Fig. 1 is seen in its metallographic structure, improves the forming property of AZ31B magnesium alloy plate from the source.In plate rolling in temperature rolling more than 300 ℃, have good plasticity, can adopt big pass deformation to be rolled.After rolling temperature was lower than 300 ℃, the plasticity of sheet material descended, and when cold rolling, deflection is about 5% first, and total deformation should be controlled in 25%, can avoid the limit occurring and split.There are a large amount of dislocations and twin tissue in the microscopic structure of the cold rolling back of AZ31B sheet material, its intensity is improved, but plasticity significantly reduce.In order to obtain best comprehensive mechanical property, need to adopt suitable annealing process to handle, eliminate Deformation structure, improve comprehensive mechanical property.See Table the mechanical property of 1 annealing AZ31B sheet material
The mechanical property of table 1 annealing AZ31B sheet material
As can be seen from the table, the comprehensive mechanical property after cold rolled annealed is significantly improved.
Respectively through 260 ℃ and 350 ℃ of annealing in process, temperature retention time is respectively 10,30,60,90,120min, its typical microstructures as the magnesium alloy plate of Fig. 2,3 after cold rolling.By the rolling AZ31B magnesium alloy plate of the inventive method, percentage elongation can reach more than 18%, and intensity can reach 270Mpa, yield tensile ratio (σ
s/ σ
b) higher; Plastic strain ratio r value can reach 1.56, and high r value helps drawing processing; The strain hardening index n value of AZ31B sheet material roll to, laterally and oblique difference little, between 0.163 and 0.181, help improving the drawing performance.Strain hardening index n value is improved through after the tandem rolling, helps improving the drawing performance.
Table 3 is the punching performance behind the AZ31B plate rolling
Punching performance behind the table 3 AZ31B plate rolling
Annotate: 0 ° of expression rolling direction in the sampling direction, 90 ° of expressions is perpendicular to rolling direction, and 45 ° of expressions and rolling direction are at 45.
As can be seen from Table 3, there is bigger difference in the mechanical property of the AZ31B sheet material of different conditions.The tensile strength of hot-rolled state is well below the corresponding index of Cold Rolled Strip, yet its percentage elongation is again than the corresponding index height of Cold Rolled Strip.The microscopic structure that the microscopic structure of warm-rolling state and Cold Rolled Strip are described is more approaching.Tensile strength is more or less the same on the hot-rolled state all directions, but horizontal percentage elongation only has 7～10%, well below rolling direction and oblique percentage elongation, illustrates that there is bigger plastic anisotropy in AZ31B magnesium alloy hot rolled plate.Cold rolling its tensile strength index than hot rolling state height near 70MPa, but its percentage elongation index is but low than hot rolling state, main cause be sheet material pass through cold rolling after, formed a large amount of twins in the Deformation structure, dislocation density is very big, intensity index is greatly improved, but plasticity index but reduce a lot.Improve the mechanical property of cold rolled sheet and just must anneal, Deformation structure produces and replys or crystallization again in annealing process, reduces dislocation density, improves comprehensive mechanical property, improves the plate stamping performance.To the simulation forming performance tests such as cupping, reaming, pull and stretch and bending by the rolling AZ31B sheet material of this method, thickness is that the sheet material limit bulging height of 1～2mm is 4.90mm; The average hole expansibility of the limit is 5.70%; The Limit Drawing coefficient is 0.788 for the first time, and the pull and stretch ratio is 1.268, minimum relative bending radius r
Min/ t is about 5.0.So at room temperature processability is good for the magnesium alloy punched sheet material of AZ31B, and is not easy to crack during cold punching, the yield rate height.
Description of drawings
Below in conjunction with accompanying drawing specific embodiments of the invention are described in further detail.
Fig. 1 is an AZ31B magnesium alloy slab ingot microscopic structure.
Fig. 2 is an AZ31B magnesium alloy hot rolled plate microscopic structure.
Fig. 3 is an AZ31B magnesium alloy cold rolled sheet microscopic structure
The specific embodiment
The magnesium alloy punched sheet material preparation method of AZ31B follows these steps to realize: 1, pressing sheet material preparation: adopt AZ31B magnesium alloy slab ingot, the chemical composition of AZ31B magnesium alloy slab ingot (mass percent than) is as following table,
Slab ingot at first will be milled by the blemish of bringing in the casting cycle by milling face, and corner angle are processed into fillet.Slab ingot is carried out homogenising again and handle in chamber type electric resistance furnace, treatment temperature is 420～450 ℃, is incubated 18 hours, and the microscopic structure after the slab ingot homogenising is handled is seen Fig. 1; 2, plate rolling: the rolling mill practice flow process of sheet material is: slab ingot → mill face → reconditioning → heating → hot rolling → cold rolling → annealing → Performance Detection → finished product, mill speed is stabilized in 1m/s, heating is carried out in chamber type electric resistance furnace, 450～460 ℃ of the start rolling temperatures of hot rolling, the hot rolling pass deflection is 15～20%, finishing temperature is 300 ± 10 ℃, heating-up temperature is 430～450 ℃, temperature retention time is 1 hour, carry out repeatedly, until sheet metal thickness is 1.5～2.5mm, and the microscopic structure of sheet material is seen Fig. 2 after the hot rolling; (2) cold rolling employing multi-pass small deformation amount is rolling, and pass deformation is about about 5%, and total cold rolling reduction is controlled at below 25%, and the thickness of finished product sheet material is 1.0～1.5mm, and the sheet material microscopic structure after cold rolling is seen Fig. 3; (3) annealing process: carry out recrystallization annealing at 260～300 ℃, temperature retention time was controlled at 60～90 minutes.
Claims (1)
1. magnesium alloy punched sheet material preparation method of AZ31B is characterized in that: follow these steps to realize:
A, pressing sheet material preparation: adopt AZ31B magnesium alloy slab ingot, slab ingot carries out homogenising in chamber type electric resistance furnace handles, and treatment temperature is 420～450 ℃, is incubated 18 hours;
B, plate rolling: the rolling mill practice flow process of sheet material is: slab ingot → mill face → reconditioning → heating → hot rolling → cold rolling → annealing → Performance Detection → finished product,
(a) start rolling temperature of wherein hot rolling is 450～460 ℃, and the hot rolling pass deflection is 15～20%, and finishing temperature is 300 ± 10 ℃, and heating-up temperature is 430～450 ℃, and temperature retention time is 1～1.5 hour, carry out repeatedly, and be 1.5～2mm until sheet metal thickness;
(b) cold rolling employing multi-pass small deformation amount is rolling, and pass deformation is about 5%, and total cold rolling reduction is controlled at below 25%, and the thickness of finished product sheet material is 1.0～1.5mm;
(c) annealing process: carry out recrystallization annealing at 260～300 ℃, temperature retention time was controlled at 60～90 minutes.
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN102400023B (en) * | 2011-11-14 | 2016-09-14 | 陈均 | A kind of preparation method of magnesium alloy for housing of electric bicycle instrument panel |
| CN103667842B (en) * | 2012-09-24 | 2016-04-13 | 中国科学院金属研究所 | A kind of low Gd content, high ductibility magnesium alloy sheet material and hot rolling process thereof |
| CN103028602B (en) * | 2012-10-30 | 2015-10-07 | 鞍钢股份有限公司 | A kind of method of rolling magnesium alloy board |
| CN104057264A (en) * | 2014-07-04 | 2014-09-24 | 重庆大学 | Magnesium alloy punch forming method |
| CN105234173A (en) * | 2015-11-17 | 2016-01-13 | 贵州大学 | Rolling machining method for improving microstructure texture and mechanical property of magnesium alloy sheet strip |
| CN109622655B (en) * | 2019-01-24 | 2023-06-23 | 吉林大学 | Variable-section rolling compression molding composite forming equipment and method for magnesium alloy |
| CN115569987A (en) * | 2022-09-09 | 2023-01-06 | 舞阳钢铁有限责任公司 | Production method of copper plate |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1749428A (en) * | 2005-09-09 | 2006-03-22 | 洛阳铜加工集团有限责任公司 | Method for processing specific shape-changing magnesium and magnesium alloy plate strip |
| CN1850433A (en) * | 2006-05-22 | 2006-10-25 | 苏州有色金属加工研究院 | Magnesium alloy product punching shaping method |
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Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN1749428A (en) * | 2005-09-09 | 2006-03-22 | 洛阳铜加工集团有限责任公司 | Method for processing specific shape-changing magnesium and magnesium alloy plate strip |
| CN1850433A (en) * | 2006-05-22 | 2006-10-25 | 苏州有色金属加工研究院 | Magnesium alloy product punching shaping method |
Non-Patent Citations (5)
| Title |
|---|
| JP特开2006-16656A 2006.01.19 |
| JP特开2007-98407A 2007.04.19 |
| JP特开平6-220597A 1994.08.09 |
| 卢志文，李焕峰，李培杰，彭伟平.AZ31B镁合金板材冲压性能的实验研究.材料导报22 3.2008,22(3),134-136. |
| 卢志文,李焕峰,李培杰,彭伟平.AZ31B镁合金板材冲压性能的实验研究.材料导报22 3.2008,22(3),134-136. * |
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