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1.
AZ31+Y+Sr镁合金板超塑成形中空洞演化   总被引:1,自引:0,他引:1  
针对添加了Y和Sr元素双辊连铸连轧(TRC)AZ31镁合金板材气胀成形过程中空洞形成进行了研究,采用了双辊连铸连轧工艺制备出1 mm厚的AZ31和AZ31+Y+Sr板材,并进行了气胀成形实验.通过宏观测量与金相观察对胀形件进行分析,结果表明:连铸连轧工艺能够有效细化晶粒,在同等温度条件下,添加了Y和Sr元素的AZ31板材其超塑性能比普通双辊连铸连轧AZ31板材有显著提高;胀形件顶部比球面的空洞尺寸大、数量多,空洞的形成经过了形核、长大和聚合三个阶段,最终导致材料的断裂.  相似文献   

2.
为了研究AZ31B型镁合金板材在室温轧制成形过程中应力应变响应规律,采用Johnson-cook本构关系对AZ31B镁合金板材在不同轧制工艺下的单道次冷轧成形进行数值模拟.分别在压下量为2%、5%、8%,应变速率分别为0.1 s~(-1)、1.0 s~(-1)、10.0 s~(-1)的条件下,开展了不同压下量及不同应变速率组合对轧件应力应变响应的模拟研究.模拟结果表明,在压下量为5%,应变速率为10.0 s~(-1)时,AZ31B镁合金板材变形过程中的局部最高应力为267.100 MPa,低于材料极限应力282.900 MPa.局部最高应变为4.454×10~(-2),低于宏观断裂应变0.2.相比其他工艺条件,此条件是较为合理的冷轧工艺.  相似文献   

3.
采用热拉伸实验测定AZ31镁合金的应力-应变曲线,依据加工硬化率理论,得到热变形过程中AZ31镁合金发生动态再结晶的临界应变和稳态应变,确定临界应变、稳态应变与塑性变形工艺参数的关系。结果表明:热变形温度和应变速率是影响AZ31镁合金动态再结晶的主要因素,提高变形温度和降低应变速率都有利于降低AZ31镁合金的临界应变和稳态应变; AZ31镁合金的动态再结晶临界应变值与Sellars经验模型的参数范围一致。  相似文献   

4.
对AZ31镁合金筋条式壁板压弯成形进行了数值模拟和实验研究。建立了有限元数值模拟的几何模型,采用有限元计算软件对AZ31镁合金筋条式壁板压弯成形进行了数值模拟研究,分析了镁合金筋条式壁板压弯成形中的温度场、应变场、应力场、模具载荷、破坏系数等分布规律,优化了变形工艺参数及模具结构。对镁合金筋条式壁板压弯成形进行了实验研究,获得了合格的镁合金筋条式壁板弯曲件。分析了镁合金筋条式壁板成形件的形状及弧度分布尺寸精度,模拟结果与实验结果相吻合,最大相对误差小于19. 1%。  相似文献   

5.
AZ31镁合金板热拉深成形工艺研究   总被引:1,自引:0,他引:1  
对AZ31镁合金板热拉深进行了实验研究,分析了凸凹模圆角半径大小、摩擦与润滑条件对AZ31镁合金板热拉深成形的影响.实验结果表明:合适的凸凹模圆角半径与有利的摩擦润滑条件可以大大减少AZ31镁合金板热拉深成形过程中发生破裂的可能性.有利于其拉深成形的顺利进行。  相似文献   

6.
空洞敏感材料超塑胀形过程的压力—时间曲线优化设计   总被引:2,自引:0,他引:2  
压力-时间曲线在超塑胀形工艺参数的选择和工艺过程优化设计中至关重要。利用刚粘塑性有限元技术对含有细微空洞超塑性材料的胀形过程进行了数值模拟,并采用最大等效应变速率恒定的压力控制策略对胀形过程压力-时间曲线进行了优化设计。以半球壳和圆筒形零件为例,对自由胀形和充模胀形两种成形方式给出了压力-时间曲线设计实例,并对计算结果进行了讨论。本计算模型可推广至其他超塑性成形问题。  相似文献   

7.
在有限元数值模拟的基础上对超塑胀形圆筒件壁厚分布进行了数值分析。为使了模拟结果更接近于实验,文中考虑了应变速率敏感、模具圆半径,等因素对壁厚的影响,同时比较了正反吹成形和普通凹模成形的零件壁厚分布状况,并对壁厚分布不均匀性及其控制技术进行探讨。  相似文献   

8.
在应变速率为0.003—3.0s^-1、温度为340~430℃的变形条件下,采用Gleeble-1500热模拟机对AZ81E镁合金进行高温热压缩变形特性研究。结果表明:流变应力随变形温度的升高和应变速率的降低而减小,峰值应力随温度的降低和应变速率的升高向应变较大处转移,进入稳态阶段的临界应变明显增大。结合Arrhenius方程并引入Zener-Hollomon参数,构建AZ81E镁合金的高温流变应力模型,其平均变形激活能为166.15kJ/mol。根据材料动态模型,计算并分析AZ81E镁合金的热加工图。利用热加工图确定热变形的流变失稳区,获得试验参数范围内的热变形过程最佳工艺参数:热加工温度范围为380~420℃,应变速率范围为0.01~0.03S^-1.  相似文献   

9.
为了研究应变速率对AZ31B变形镁合金力学性能的影响,试验温度为室温、150℃时,对AZ31B变形镁合金进行拉伸试验,并记录抗拉强度和屈服强度,计算延伸率.通过扫描电镜观察拉伸断口形貌,结果表明,随着应变速率的提高,AZ31B变形镁合金的抗拉强度和屈服强度都随之提高,而延伸率却逐渐降低;随着温度的升高,同一应变速率下的抗拉强度和屈服强度降低,而延伸率大幅度升高.通过观察扫描断口形貌发现,合金表现为韧性断裂,且随着应变速率的降低,韧窝逐渐增多.  相似文献   

10.
为了研究高应变速率下AZ31B镁合金动态力学行为各向异性,采用分离式霍普金森压杆(SHPB)对沿挤压方向(ED)、法向(ND)及横向(TD)加工的AZ31B镁合金在应变速率为1.058~2.500s-1范围内进行冲击压缩实验,并采用扫描电镜观察压缩断口形貌.结果表明:高应变速率下AZ31B镁合金沿ED方向和ND方向有明显的应变强化现象,而沿TD方向应力对应变速率不敏感;随应变速率的增加,不同载荷方向屈服强度与最大应力值的差值变化程度有所不同,其中沿ND方向差值变化最大,沿TD方向差值变化最小;通过观察扫描断口形貌发现,在高应变速率下AZ31B镁合金在不同载荷方向下的断裂方式均为解理断裂.  相似文献   

11.
研究间断变形工艺对AZ31镁合金超塑性的影响。结果表明,当温度为400-440℃、应变速率小于5×10^-4s^-1时,间断变形工艺可以显著提高AZ31镁合金的超塑性。计算了空洞体积分数与空洞数量的关系。结果表明,空洞体积分数与空洞数量呈正比。对拉伸试样断口形貌的分析表明,间断变形减少了空洞数量,因而减小了空洞体积分数,提高了超塑性伸长率。  相似文献   

12.
13.
为了研究帽状试样AZ31B镁合金和6065铝合金在动态压缩变形过程中的温度、应力与应变演变规律,采用Johnson-Cook本构方程和累积塑性损伤方程进行了数值模拟,运用有限元软件ANSYS/LS-DYNA模拟了AZ31B镁合金和6065铝合金帽状试样的动态变形过程.结果表明,两种合金的裂纹萌生和扩展过程相似,局域化变形带内塑性应变由内向外对称分布.相比于AZ31B镁合金,6065铝合金的塑性应变影响区域更为狭小,其应变和应变率硬化效果更强.6065铝合金的变形温度能够达到其动态再结晶临界点,因而易于绝热剪切带的形成.  相似文献   

14.
The kinetics of recrystallization for twin-roll casting AZ31 magnesium alloy with different thicknesses during homogenization was analyzed.It is shown that fine grains are first formed at the boundaries of deformed bands in the twin-roll casting slab.The recrystallized grains with no strain are gradually substituted for the deformed microstructure of twin-roll casting AZ31 magnesium alloy.The incubation temperature and time for the recrystallization of a twin-roll casting AZ31 magnesium alloy strip with a thickness of 3 mm are lower and shorter than those of the 6-mm thick strip,respectively.The 3-mm thick twin-roll casting magnesium alloy has finer grains than the 6-mm thick strip.The activation energies of recrystallization for twin-roll casting AZ31 magnesium alloy slabs with the thickness of 3 and 6 mm are 88 and 69 kJ/mol,respectively.The kinetics curves of recrystallization for twin-roll casting AZ31 magnesium alloy were obtained.  相似文献   

15.
Superplastic forming has been extensively applied to manufacture parts and components with complex shapes or high-precisions. However, superplastic formation is in multi-stress state. In a long time, uniaxial tensile constitutive equation has been directly generalized to deal with multi-stress state. Whether so doing is feasible or not needs to be proved in theory. This paper first summarizes the establishing processes of superplastic tensile and bulging constitutive equation with variable m, and, using the analytical expressions of equivalent stress a and equivalent strain rate ε of free bulge based on the fundamentals of continuum medium plastic mechanics, derives the analytical expressions of optimum loading rules for superplastic free bulge. By comparing the quantitative results on typical superplastic alloy ZnAI22, it is shown that one-dimensional tensile constitutive equations cannot be directly generalized to deal with two-dimensional bulging quantitative mechanical problems; only superplastic b  相似文献   

16.
The plastic deformation simulation of AZ31 magnesium alloy at different elevated temperatures (from 473 to 723 K) was performed on Gleeble-1500 thermal mechanical simulator at the strain rates of 0.01, 0.1, 1, 5 and 10 s-1 and the maximum deformation degree of 80%. The relationship between the flow stress and deformation temperature as well as strain rate was analyzed. The materials parameters and the apparent activation energy were calculated. The constitutive relationship was established with a Zener-Holl...  相似文献   

17.
It was investigated that the superplastic mechanical properties of fine-grained ZK60 magnesium alloy sheets at the temperature range of 200-420 ℃ and strain rate range of 5.56 × 10-4 -5.56 ×10-2 s-1 by tensile tests.And the microstructure evolution during the superplastic deformation of ZK60 magnesium alloy was examined by metallurgical microscope and transmission electronic microscope (TEM).The results showed that fine-grained ZK60 magnesium alloy starts to exhibit superplasticity from 250 ℃ and the maximum elongation is about 1106% at 400 ℃ and 5.56 × 10-4 s-1.The strain rate sensitivity is significantly enhanced with the increase of temperature and with the decrease of strain rate.The predominate superplastic mechanism of ZK60 magnesium alloy is grain boundary slide (GBS) at the temperature range of 300-400 ℃.The grains of ZK60 alloy remain equaxial after superplastic deformation,and dynamic continuous recrystallization (DCRX) is an important softening mechanism and grain stability mechanism during the superplastic deformation of the alloy.The curved grain boundaries and crumpled bands at grain boundaries after deformation prove GBS generates during superplastic deformation of ZK60 magnesium alloy.  相似文献   

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