纳米铝晶界内耗峰的连续变温研究

采用低温球磨结合热压烧结技术制备了块体纳米铝晶体材料,在多功能内耗仪上采用受迫振动连续变温(25～450℃)的方式测量了纳米铝材料在低频率(0.2～3.0Hz)条件下的内耗和相对动力学模量。结果表明,纳米铝晶体材料受迫振动时,在升温和降温的内耗-温度谱上均出现一个内耗峰;伴随着内耗峰的出现,相对动力学模量明显下降;随着离散振动频率的增加,内耗峰峰位向高温方向移动,说明该内耗峰具有弛豫性;根据Arrhenius关系,得到该内耗峰的激活能为(2.21±0.04)×10-19 J、指数前因子τ0为10-14 s,表明该内耗峰是晶界内耗峰,其机制为铝原子在铝/铝晶界的自扩散。     

Al-Sn 合金中两个不同类型的内耗峰

Al-Sn 合金多晶样品中,在传统晶界峰的高温侧发现了两个不同类型的内耗峰(记作 P_1,P_2峰),它们在单晶中均消失,因而与晶界相关。P1与晶界峰有消长关系,对时效和退火温度敏感,仅在降温过程中出现,是过程峰,存在于 Al-0.008wt-%Sn 和 Al-0.0135wt-%Sn 多晶试样中;P_2与晶粒尺寸和样品尺寸相关,是稳定的内耗峰,存在于 Al-0.067wt-%Sn 和 Al-0.136wt-%Sn 多晶试样中。P_1,P_2峰分别来源于被Sn 原子非平衡偏聚的细晶界和含有 Al-Sn 沉淀粒子的粗晶界。     

热处理对喷射共沉积SiCP/6061Al复合材料内耗峰的影响

采用喷射共沉积方法制备了SiC_P/6061Al复合材料,研究了五种热处理工艺对其阻尼性能和内耗峰的影响。结果表明:各种热处理状态试样,在150~200℃范围内均出现温度内耗峰,且随频率增加该峰峰位向高温移动,峰高增加。通过Arrhenius方程测得内耗峰的激活能均高于1eV;另外,不同的淬火处理对该内耗峰有明显影响,当淬火冷却速度高于水淬时,随冷却速度的加大,内耗峰峰位向高温移动。     

恒速拉伸过程中纯 Cu 晶界内耗峰的变化

研究了纯 Cu 晶界内耗峰和模量弛豫在不同温度下恒速拉伸形变过程中的变化。考查了以下四种晶界弛豫参量的变化:(a)峰温,(b)峰高,(c)激活能,(d)模量弛豫强度。所得结果表明:在形变过程中晶界强度是变化着的,并且这种变化与断裂类型有密切关系。本文进一步肯定并扩展了我们以前在蠕变方面的工作。     

一种高铝多元合金钢的奥氏体晶界显示技术

基于化学侵蚀基本原理,采用控温控时水浴锅,结合光学显微镜观察,研究了1.79Al-1.5Mn-1.09Cr基高铝多元合金钢淬火原奥氏体晶界显示技术。结果表明:最佳侵蚀剂配方为30mL饱和苦味酸水溶液+1~2滴氢氟酸+适量海鸥牌洗发膏,不同淬火加热温度下试验钢的原奥氏体晶界可通过调整海鸥牌洗发膏用量而清晰显示;试验钢最佳侵蚀温度为室温;高温淬火试样较低温淬火试样的原奥氏体晶界更易被侵蚀而清晰显示。     

Mn-Fe基合金的反铁磁与高阻尼

采用动力学分析（DMA）和透射电子显微分析（TEM）等实验方法,研究了含锰45．9％－86．4％（原子分数）范围Mn-Fe-(Cu)合金的反铁磁转变,马氏体相变及高阻尼特性。当锰含量超过71％（原子分数）时合金在变温过程中发生顺磁－反铁磁转变引起模量的剧烈变化。在尼尔点（TN)以下的反铁磁状态－200℃温区内出现一个10^-1数量级内耗的高阻尼区。随着含锰量的增加该区内逐渐显示出两个分立的内耗峰。确定了其中高温端的内耗峰为马氏体相变的贡献而低温端的内耗峰则纯属孪晶界的驰豫型内耗。文中测定了驰豫过程的激活能,讨论了合金呈现高阻尼与两种相变的关系。     

热轧态LT24铝合金溶质原子的偏聚规律

采用原子探针层析技术(APT)等测试手段分析了LT24铝合金热轧后合金元素的偏聚规律。结果表明:热轧态铝合金晶粒内部有成分为Al0.5Mg(Si0.7Cu0.3)的析出相,析出相与基体之间的界面处没有元素偏聚。溶质原子Mg、Si、Cu在晶界处偏聚,在晶界处的偏聚规律与晶粒内部的相反,Cu的偏聚倾向远大于Si和Mg,晶界处Cu的含量达到基体Cu含量的45倍左右。基于实验结果,讨论了合金元素偏聚的规律及其对材料性能的影响。     

一种显示奥氏体晶界的方法

1 实验内容 本实验采用化学侵蚀法对20CrMnTi,40,40Cr,35CrMo,8CrSiMoV五种钢材的淬火态、低温回火态和高温回火态三种不同热处理状态下的原奥氏体晶界进行显示。具体热处理工艺:淬火880℃,保温30min,水冷;回火分别在200℃,600℃保温1h,空冷。 2 试剂配方及注意事项     

喷射沉积Al-3.3Fe-10.7Si合金的组织、韧性及内耗性能研究

利用喷射沉积工艺制备Al-3.3Fe-10.7Si合金坯,经挤压制成试样.研究了合金组织、韧性及内耗行为,得出该合金在60～250℃温度范围产生的内耗峰,是由于晶界滑动弛豫引起的,弛豫过程激活能为172.2kJ/mol.在内耗峰位置晶界滑动消耗部分振动能,合金韧性在此处出现极大值.     

C和B的含量对K417G镍基高温合金的凝固行为和高温持久性能的影响

对不同C、B含量的K417G合金进行DTA分析、等温淬火实验和950℃/235 MPa持久性能测试,并观察其组织形貌,研究了C、B含量对K417G镍基高温合金的凝固行为和高温持久性能的影响。结果表明,在合金的凝固期间C含量影响碳化物的析出温度和初生碳化物的含量,且随着C含量的提高而提高;共晶组织的析出温度主要受B元素含量影响,且共晶含量随着B含量的提高而提高。合金在950℃/235MPa条件下持久变形期间其断裂机制为裂纹在晶界处萌生并沿晶界扩展,晶界处的MC型碳化物分解成富Cr的M₂₃C₆型碳化物而使晶界的稳定性降低;在合金成分范围内提高B元素含量能改善合金在高温变形期间的晶界强度,因此适当降低合金中的C含量和提高B含量有助于改善合金的高温持久性能。     

Grain growth and grain orientation distribution of Al-Mg alloys

Grain growth behaviour of Al–Mg alloys containing 0.3, 2.7 and mass% Mg was investigated focusing on the spatial distribution of grain orientation and grain boundary character. In Al–0.3 mass% Mg alloy the cube texture developed at the first stage and then the texture declined accompanied with abnormal grain growth of non-cube grains at the second stage. The development of cube grains was suppressed by an increase of solute Mg atoms. The texture change depended strongly on spatial distribution of grain boundary character and cube clusters.     

锶镁共掺对Na0.5Bi0.5TiO3氧离子导体电学性能的影响分析

通过固相反应法制备单一结构的锶镁共掺的Na0.5Bi0.48Sr0.02Ti0.98Mg0.02O2.97氧离子导体,利用交流阻抗谱和内耗温度谱分别研究锶镁共掺对Na0.5Bi0.5TiO3材料晶粒电导率及氧离子扩散的影响。在593K时,Na0.5Bi0.48Sr0.02Ti0.98Mg0.02O2.97材料的晶粒电导率可以达到5.31×10^-4S/cm,比母体Na0.5Bi0.5TiO3材料在同温度下的晶粒电导率高一个数量级,甚至超过了Na0.5Bi0.5Ti0.98Mg0.02O2.98样品在673K温度下的晶粒电导率。在锶镁共掺的Na0.5Bi0.48Sr0.02Ti0.98Mg0.02O2.97材料中观察到一个氧弛豫内耗峰,其弛豫参数为:E=0.85eV,τ0=7.4×10^-14s。结合弛豫参数和结构分析,Sr^2+的掺杂在一定程度上可以增大氧离子扩散的自由体积,较大的自由体积、较高的可动氧空位浓度和较好的氧空位可动性是NBT-SrMg2样品晶粒电导率相较于NBT-Mg2样品大幅提高的主要原因。     

The effects of trace Sc and Zr on microstructure and internal friction of Zn–Al eutectoid alloy

The damping properties of Zn–22 wt.% Al alloys without and with Sc (0.55 wt.%) and Zr (0.26 wt.%) were investigated. The internal friction of the determined by the microstructure has been measured in terms of logarithmic decrement (δ) using a low frequency inverted torsion pendulum over the temperature region of 10–230 °C. An internal friction peak was separately observed at about 218 °C in the Zn–Al alloy and at about 195 °C in Zn–Al–Sc–Zr alloy. The shift of the δ peak was found to be directly attributed to the precipitation of Al₃(Sc, Zr) phases from the alloy matrix. We consider that the both internal friction peak in the alloy originates from grain boundary (GB) relaxation, but the grain boundary relaxation can also be affected by Al–Sc–Zr intermetallics at the grain boundaries, which will impede grain boundary sliding. In addition, Al–Sc–Zr intermetallics at the grain boundaries can pin grain boundaries, and inhibit the growth of grains in aging, which increases the damping stability of Zn–22 wt.% Al alloy.     

Microstructure and internal friction of spray deposited Al-3.3Fe-10.7Si alloy

Al-3.3Fe-10.7Si alloy has been experimentally made with spray deposition technology. The internal friction of the alloy which was directly associated with the microstructures under spray deposited, extruted and heat treated conditions has been investigated using a low frequency inverted torsion pendulum over the temperature region of 10–300 °C. An internal friction peak was observed in the temperature range 50–250 °C in the present alloy. The Q^-1 peak decreased after extruted and in subsequent to the earliness of isothermal annealing, which was found to be directly attributed to the precipitation of FeAl₂ and Al– Fe– Si intermetallics from the supersaturated aluminium alloy matrix. We suggest that the internal friction peak in the alloy originates from grain boundary relaxation, but the grain boundary relaxation can also be affected by FeAl₂ and Al– Fe– Si intermetallics at the grain boundaries, which will impede grain boundary sliding.     

Grain Boundary Sliding at Serrated Grain Boundaries

A constitutive model is developed for grain boundary sliding (GBS) at serrated grain boundaries. Based on a previously developed GBS model, using the dynamics of grain boundary dislocation pile-up, the present model takes the average of the sliding rate over the characteristic dimensions of grain boundary serrations. Thus, a geometric factor is introduced to account for the effects of serration wave length and amplitude on the GBS rate, as compared to the GBS rate at planar boundaries. By considering the role of grain boundary shear stress in stress balancing, the proposed model removes the singularity at planar boundaries which exists in the diffusion-controlled GBS model at serrated grain boundaries. The modified model describes very well the transient creep of complex Ni-base superalloys with and without grain boundary serrations and should be suitable for other engineering alloys (with the exception of columnar grained and single crystal alloys).     

大塑性变形制备超细晶/纳米晶Al-Mg铝合金的研究进展

近年来,大塑性变形(SPD)制备具有先进结构和功能的超细晶和纳米晶Al-Mg铝合金的研究取得了很大进展。SPD后,合金的晶粒显著细化、位错密度提高及有非平衡晶界和晶界偏析形成,这些微观结构导致合金的强度、硬度大幅提高。然而,SPD合金的塑性普遍较低。综述了SPD制备的Al-Mg铝合金在结构和性能方面的一些最新研究成果。     

Internal friction of powder metallurgy (P/M) and ingot metallurgy (I/M) Al–Fe alloys at elevated temperature

Low-frequency internal friction measurements have been carried out on the powder metallurgy (P/M) and ingot metallurgy (I/M) Al–Fe alloy. Internal friction peaks can be seen at about 820–830 K and 530–620 K in the I/M alloys, but not in the P/M alloys. The former is probably due to the grain-boundary relaxation and the latter to recrystallization. Activation energies for the grain-boundary relaxation are estimated to be in two ranges: one is between 100 and 130 kJ mol–1 and the other is between 200 and 210 kJ mol–1, according to the iron content and fabrication processes. The high activation energy is given by the low iron content I/M alloys having a bamboo-like grain. It is suggested that such a difference in the activation energy is due to whether or not the solute iron diffuses into the grain boundary to lower the grain boundary energy.     

The change of grain boundary internal friction peak during high temperature deformation at different modes

The change of grain boundary internal friction peak during high temperature deformation at different modes (i.e., static tensile creep, cyclic tensile creep, and cyclic reverse torsion) in high purity aluminum was studied in conjunction with microstructure examinations. It was observed that the internal friction peak decreased with increasing plastic strain for all the modes, indicating that grain boundary sliding was degraded by the deformation. Nevertheless, at the same strain the decrement of internal friction was different for different modes, in particular smallest for reverse torsion. The origin of the decrease of internal friction and the difference among different modes is interpreted in the light of microstructure observations.