Researchers have determined hardness for the magnesium alloyin HV Vickers micro hardness. Most of the researchers observed thehardness to be improved through number of ECAP passes andannealing [28,29] while for some of the researchers it showedthe decreased in total hardness [25,17,18] due to the different processing conditions and microstructure stability. The hardness ofmagnesium alloy improved by heat treatment, aging temperatures[34].Most of the researchers have investigated the mechanical properties of magnesium alloy, it is observed that young’s modulus,yield stress, ultimate tensile stress were higher after ECAP andHPT with additional annealing and cooling in water than in air[26,20,25,27,1] and increased in ductility is found due to twinningreinforcement of slip on basal plane. Shear band in tensile, whichshowed good ductility [1]; the particle size effects the tensilestrength, the tensile strength can be improved by thermal treatment [26,20] or extrusion [22].The mechanism and mode of failure during tensile testing ofmagnesium alloy has been reported by [31] he observed that theinitiation and growth of shear cracks leading to the grain size toenlarge and moves one away from the crack leads to failure ofthe material matrix. [9] observed the failure for the tensile testingof magnesium alloy occurs by ductility failure, and dimples variations leads to microstructure failure. [26,20] observed the failurefor AZ91 alloy due to the brittle fracture, micro pores, while forAZ61 alloy is due to ductile fracture.Compressive strength was found to be increased for magnesiumalloy after hardening treatment at below 200 C and fell belowbeyond 200 C [5]. The compressive strength can be improved bytwining mechanism with ECAP passes [30].The researchers found increase in texture after two ECAP passesat 150 C, as the old texture was replaced by the newly formedstrong texture having basal slips [33]; while the other researchersfor texture found that the material after ECAP passes through routeBc, C showed high basal slips [21,12].The toughness for magnesium alloy is increased as the materialprocessed by ECAP passes, as the grain size decrease and increasein toughness is observed leading to increase in Charpy impacttoughness [30] and [35].
研究人员已经<br>以HV维氏显微硬度确定了镁合金的硬度。大多数研究人员观察到,<br>通过进行ECAP次数和<br>退火可以提高硬度[28,29],而对于一些研究人员来说<br>,由于不同的加工条件和微观结构,总硬度降低了[25,17,18]。稳定性。<br>通过热处理,时效温度提高了镁合金的硬度<br>[34]。<br>大多数研究人员已经研究了镁合金的力学性能,发现在水中进行额外的退火和冷却的<br>ECAP和<br>HPT后,杨氏模量,屈服应力,极限拉伸应力要比空气中的高。<br>[26,20,25,27,1]和延展性的增加是由于<br>在基面上的孪生滑移加强。剪切带处于拉伸状态,<br>表现出良好的延展性[1];粒径影响抗拉强度<br>,可通过热处理[26,20]或挤压[22]来提高抗拉强度。[31]已经报道了镁合金<br>拉伸试验过程中的失效机理和模式,<br>他观察到<br>剪切裂纹的萌生和扩展导致晶粒尺寸<br>增大并远离裂纹,导致<br>材料基体失效。。[9]观察到拉伸试验失败<br>镁合金的延展性是由于延展性破坏而产生的,并且酒窝的变化导致微观结构的破坏。[26,20]观察到<br>AZ91合金的失效是由于脆性断裂,微孔,而<br>AZ61合金的失效是由于韧性断裂。<br>发现<br>在200°C以下进行硬化处理后,镁合金的抗压强度增加,而在200°C以下则下降<br>[5]。可以通过<br>带有ECAP通道的缠绕机制来提高抗压强度[30]。<br>研究人员发现,<br>在150°C下经过两次ECAP后,质地增加了,这是因为旧质地被新形成的<br>具有基层滑移的坚固质地所代替[33];而其他研究人员<br>对于质地,发现ECAP通过<br>Bc路线后的材料C表现出较高的基层滑移[21,12]。<br>镁合金的韧性随着<br>通过ECAP处理的材料的通过而增加,随着晶粒尺寸的减小和<br>韧性的增加而导致夏比冲击<br>韧性[30]和[35]增大。
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研究人员已经测定了镁合金的硬度<br>在高压维氏显微硬度。大多数研究人员观察到<br>通过ECAP焊道数和<br>退火[28,29]对一些研究人员来说<br>由于不同的加工条件和组织稳定性,总硬度[25,17,18]降低。的硬度<br>镁合金经热处理、时效温度提高<br>[34]。<br>大多数研究者都对镁合金的力学性能进行了研究,发现镁合金的杨氏模量,<br>ECAP后屈服应力、极限拉应力均高于ECAP<br>在水中比在空气中进行额外退火和冷却的HPT<br>[26,20,25,27,1]并且由于孪晶,塑性增加<br>基底面滑移加固。拉伸剪切带<br>具有良好的延展性[1];颗粒大小影响拉伸<br>强度,拉伸强度可以通过热处理[26,20]或挤压[22]来提高。<br>拉伸试验中的破坏机理和破坏模式<br>据[31]报道,镁合金<br>剪切裂纹的萌生和扩展导致晶粒尺寸<br>扩大并移动一个远离裂缝导致<br>材料矩阵。[9] 观察拉伸试验的失败<br>镁合金发生塑性破坏,韧窝变化导致组织破坏。[26,20]观察到故障<br>对于AZ91合金由于脆性断裂、微孔,而对于<br>AZ61合金为韧性断裂。<br>镁的抗压强度增加<br>合金经200℃以下淬火处理后下降到<br>超过200摄氏度[5]。抗压强度可通过<br>带ECAP通道的缠绕机构[30]。<br>研究人员发现,经过两次ECAP检查后,织物的质地有所增加<br>在150℃时,由于旧的纹理被新形成的纹理所取代<br>具有基底滑移的坚固结构[33];而其他研究人员<br>对于纹理发现,ECAP后的材料通过路径<br>Bc、C表现出较高的基底滑移[21,12]。<br>镁合金的韧性随着材料的增加而增加<br>通过ECAP道次加工,随着晶粒尺寸的减小和增大<br>在韧性方面观察到导致夏比冲击增加<br>韧性[30]和[35]。
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