载能碳离子撞击石墨烯中Stone-Wales缺陷的动力学研究

采用分子动力学模拟方法,研究了载能碳离子撞击石墨烯中Stone-Wales缺陷的动力学过程,计算了Stone-Wales缺陷中初级碰撞原子的离位阈能和载能碳离子使其移位的入射阈能,并与完美石墨烯结构计算结果进行对比。通过分析初级碰撞原子与入射离子动能和势能随时间的变化关系,研究了碰撞过程中能量转移过程。研究结果表明,初级碰撞原子产生离位并最终脱离石墨烯体系的最小能量为25.0 eV;当初始动能为23.0 eV时,Stone-Wales缺陷中2个七元环共用的碳-碳键旋转90°形成了完美的石墨烯结构;使Stone-Wales缺陷中初级碰撞原子发生离位的载能碳离子最小入射能为41.0 eV。     

碳离子碰撞单壁碳纳米管的动力学

采用分子动力学方法研究了碳离子碰撞碳纳米管中顶位、键中心和六元环中心的动力学过程。通过分析低、中、高3种入射能分别对碰撞过程的影响,探索了典型缺陷形成的微观演化过程。研究结果表明,碰撞碳纳米管中不同空间位置,其碰撞结果差异较大,其中顶位碰撞阈能最低,约为20 eV;碰撞六元环中心时碳管会发生严重变形,损伤最为严重。通过分析入射离子动能,碳纳米管热动能、质心动能以及势能随时间的演化规律,阐述了碰撞过程中的能量转移机制。     

碳离子碰撞单壁碳纳米管的动力学

采用分子动力学方法研究了碳离子碰撞碳纳米管中顶位、键中心和六元环中心的动力学过程。通过分析低、中、高3种入射能分别对碰撞过程的影响,探索了典型缺陷形成的微观演化过程。研究结果表明,碰撞碳纳米管中不同空间位置,其碰撞结果差异较大,其中顶位碰撞阈能最低,约为20 e V;碰撞六元环中心时碳管会发生严重变形,损伤最为严重。通过分析入射离子动能,碳纳米管热动能、质心动能以及势能随时间的演化规律,阐述了碰撞过程中的能量转移机制。     

改性氧化石墨烯去除重金属离子的分子动力学模拟

通过硅烷化反应在氧化石墨烯(Graphene oxide, GO) 表面嫁接螯合官能团N-(三甲氧基硅丙烷)乙二胺三酸(EDTA-Si), 得到改性氧化石墨烯(GO-EDTA), 采用分子动力学模拟在分子水平上研究了Pb²⁺在GO-EDTA 表面的动态吸附分布、 构象及动力学性质, 比较了Pb²⁺和单价Na⁺离子在氧化石墨烯上的吸附行为, 模拟了GO-EDTA与Ca²⁺相互作用, 与Pb²⁺的吸附行为进行了对比. 模拟结果表明, Pb²⁺和Na⁺的吸附位点是GO-EDTA 体系中的羧基, 而非氧化石墨烯表面的羟基; Pb²⁺和 Na⁺ 与羧基的吸附构象不同, 前者吸附构象以摩尔比2:1为主, 即两个羧基对一个Pb²⁺离子, 而后者更多倾向于摩尔比1:1的吸附模式, 即一个羧基对一个Na⁺离子; Pb²⁺离子相对于Ca²⁺和Na⁺离子, 形成的COO^--Pb²⁺离子对构象越过的能垒最低, 但是破坏该离子对构象时能垒较高, 表明Pb²⁺离子在氧化石墨烯膜上表现出良好的吸附性.     

缺陷石墨烯吸附Au、Ag、Cu的第一性原理计算

采用基于密度泛函理论的投影缀加波方法研究了Au、Ag、Cu吸附在缺陷石墨烯单侧和双侧的体系,对吸附体系的吸附能、磁性、电荷转移和电子结构进行了计算和分析. 缺陷石墨烯吸附Au、Ag、Cu体系的吸附能比本征石墨烯增加2 eV以上,说明三种金属原子更容易吸附在缺陷位置;吸附体系的电荷密度差分和电子结构的结果表明,Au、Ag、Cu与缺陷石墨烯之间均为化学吸附. 计算吸附体系的磁性发现,单侧吸附时三种吸附体系均有磁性,磁矩大约为1μ_B;双侧吸附时,三种吸附体系磁矩大约为2μ_B.     

锯齿形单壁碳纳米管的穿透能研究

基于分子动力学方法,研究了载能碳离子碰撞锯齿形单壁碳纳米管过程中初级碰撞原子(PKA)的运动过程和能量变化过程.分析了手性指数为(2n+1,0)(n=2~9)的单壁碳纳米管中PKA的穿透能与载能碳离子入射能间的关系.结果表明,穿透能与入射能之间呈线性增长关系,线性变化的斜率与碳纳米管直径有关.通过分析PKA势能随模拟时间的变化规律,阐述了初级碰撞原子的穿透能随入射能的增加而增加的物理机制.     

缺陷石墨烯吸附Au、Ag、Cu的第一性原理计算

采用基于密度泛函理论的投影缀加波方法研究了Au、Ag、Cu吸附在缺陷石墨烯单侧和双侧的体系,对吸附体系的吸附能、磁性、电荷转移和电子结构进行了计算和分析.缺陷石墨烯吸附Au、Ag、Cu体系的吸附能比本征石墨烯增加2 eV以上,说明三种金属原子更容易吸附在缺陷位置;吸附体系的电荷密度差分和电子结构的结果表明,Au、Ag、Cu与缺陷石墨烯之间均为化学吸附.计算吸附体系的磁性发现,单侧吸附时三种吸附体系均有磁性,磁矩大约为1μB;双侧吸附时,三种吸附体系磁矩大约为2μB.     

参杂缺陷石墨烯的高分子复合材料导热特性分子动力学模拟

Polymers are widely used advanced materials composed of macromolecular chains, which can be found in materials used in our daily life. Polymer materials have been employed in many energy and electronic applications such as energy harvesting devices, energy storage devices, light emitting and sensing devices, and flexible energy and electronic devices. The microscopic morphologies and electrical properties of the polymer materials can be tuned by molecular engineering, which could improve the device performances in terms of both the energy conversion efficiency and stability. Traditional polymers are usually considered to be thermal insulators owing to their amorphous molecular chains. Graphene-based polymeric materials have garnered significant attention due to the excellent thermal conductivity of graphene. Advanced polymeric composites with high thermal conductivity exhibit great potential in many applications. Therefore, research on the thermal transport behaviors in graphene-based nanocomposites becomes critical. Vacancy defects in graphene are commonly observed during its fabrication. In this work, the effects of vacancy defects in graphene on thermal transport properties of the graphene-polyethylene nanocomposite are comprehensively investigated using molecular dynamics (MD) simulation. Based on the non-equilibrium molecular dynamics (NEMD) method, the interfacial thermal conductance and the overall thermal conductance of the nanocomposite are taken into consideration simultaneously. It is found that vacancy defects in graphene facilitate the interfacial thermal conductance between graphene and polyethylene. By removing various proportions of carbon atoms in pristine graphene, the density of vacancy defects varies from 0% to 20% and the interfacial thermal conductance increases from 75.6 MW·m⁻²·K⁻¹ to 85.9 MW·m⁻²·K⁻¹. The distinct enhancement in the interfacial thermal transport is attributed to the enhanced thermal coupling between graphene and polyethylene. A higher number of broken sp² bonds in the defective graphene lead to a decrease in the structure rigidity with more low-frequency (< 15 THz) phonons. The improved overlap of vibrational density states between graphene and polyethylene at a low frequency results in better interfacial thermal conductance. Moreover, the increase in the interfacial thermal conductance induced by vacancy defects have a significant effect on the overall thermal conductance (from 40.8 MW·m⁻²·K⁻¹ to 45.6 MW·m⁻²·K⁻¹). In addition, when filled with the graphene layer, the local density of polyethylene increases on both sides of the graphene. The concentrated layers provide more aligned molecular arrangement, which result in better thermal conductance in polyethylene. Further, the higher local density of the polymer near the interface provides more atoms for interaction with the graphene, which leads to stronger effective interactions. The relative concentration is insensitive to the density of vacancy defects. The reported results on the thermal transport behavior of graphene-polyethylene composites provide reasonable guidance for using graphene as fillers to tune the thermal conduction of polymeric composites.     

石墨烯/环氧复合材料导热性能的研究进展

石墨烯作为时下最热门的纳米材料,吸引了国内外众多科研工作者的注意力。而石墨烯所具有的超高导热性能,使其在环氧导热复合材料中有着巨大的应用前景。本文主要综述了当前石墨烯/环氧复合材料导热性能的研究进展,详细介绍了石墨烯的尺寸、与其它填料的复配以及石墨烯表面改性等因素对导热性能的影响。此外,还分析了复合材料的微观结构对导热性能的影响。最后,对导热型石墨烯/环氧复合材料的发展进行了展望,并指出了该领域存在的技术难点和未知机理。     

Predicting relative binding affinities of non-peptide HIV protease inhibitors with free energy perturbation calculations

The relative binding free energies in HIV protease of haloperidol thioketal (THK) and three of its derivatives were examined with free energy calculations. THK is a weak inhibitor (IC50 = 15 M) for which two cocrystal structures with HIV type 1 proteases have been solved [Rutenber, E. et al., J. Biol. Chem., 268 (1993) 15343]. A THK derivative with a phenyl group on C2 of the piperidine ring was expected to be a poor inhibitor based on experiments with haloperidol ketal and its 2- phenyl derivative (Caldera, P., personal communication). Our calculations predict that a 5-phenyl THK derivative, suggested based on examination of the crystal structure, will bind significantly better than THK. Although there are large error bars as estimated from hysteresis, the calculations predict that the 5-phenyl substituent is clearly favored over the 2-phenyl derivative as well as the parent compound. The unfavorable free energies of solvation of both phenyl THK derivatives relative to the parent compound contributed to their predicted binding free energies. In a third simulation, the change in binding free energy for 5-benzyl THK relative to THK was calculated. Although this derivative has a lower free energy in the protein, its decreased free energy of solvation increases the predicted G(bind) to the same range as that of the 2-phenyl derivative.     

Dispersion of Graphene Sheets in Aqueous Solution by Oligodeoxynucleotides

Applications of graphene sheets in the fields of biosensors and biomedical devices are limited by their insolubility in water. Consequently, understanding the dispersion mechanism of graphene in water and exploring an effective way to prepare stable dispersions of graphene sheets in water is of vital importance for their application in biomaterials, biosensors, biomedical devices, and drug delivery. Herein, a method for stable dispersion of graphene sheets in water by single‐stranded oligodeoxynucleotides (ssODNs) is studied. Owing to van der Waals interactions between graphene sheets, they undergo layer‐to‐layer (LtL) aggregation in water. Molecular dynamics simulations show that, by disrupting van der Waals interaction of graphene sheets with ssODNs, LtL aggregation of graphene sheets is prevented, and water molecules can be distributed stably between graphene sheets. Thus, graphene sheets are dispersed stably in water in the presence of ssODNs. The effects of size and molarity of ssODNs and noncovalent modification of graphene sheets are also discussed.