锂电池外文文献阅读笔记

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锂电池回馈电流英文

锂电池回馈电流英文全文共四篇示例，供读者参考第一篇示例：Lithium-ion batteries are popular for their high energy density, long lifespan, and rechargeable capabilities. However, they are not without limitations, one of which is the phenomenon known as "battery feedback current." In this article, we will explore what battery feedback current is, how it affects lithium-ion batteries, and some ways to mitigate its impact.第二篇示例：Lithium battery feedback current refers to the electrical current that flows back into the battery during charging or discharging. In simple terms, it is the flow of electric charge that occurs when a lithium battery is connected to an external power source. This phenomenon is important to understand as it can have a significant impact on the performance and lifespan of the battery.第三篇示例：Feedback current, or also known as parasitic current, refers to the phenomenon where a small amount of current flows back into the battery during the charging process. This can happen due to various reasons such as the formation of dendrites, side reactions, and impedance mismatch within the battery pack. While feedback current may seem like a minor issue, it can have a significant impact on the performance and lifespan of the battery.第四篇示例：Lithium-ion batteries are widely used in many electronic devices and electric vehicles due to their high energy density and long lifespan. However, as these batteries age, they may start to exhibit higher levels of feedthrough current, also known as feedback current. This phenomenon occurs when the battery is not in use, but still generates a small amount of current that flows in the opposite direction from the intended charging or discharging direction.Feedback current can have several negative effects on the battery and the device it powers. One of the main concerns is the potential for overcharging, which can lead to thermal runaway and even cause the battery to catch fire or explode. This is aserious safety hazard that can be avoided by monitoring and controlling the feedback current in lithium-ion batteries.Another issue caused by feedback current is theself-discharge of the battery. When the battery is not in use, the feedback current can slowly drain the stored energy, reducing the overall lifespan of the battery. This can be particularly problematic for devices that are not used frequently or for long periods of time, as the battery may lose its charge faster than expected.To mitigate the effects of feedback current, manufacturers are constantly researching and developing new technologies and materials to improve the performance of lithium-ion batteries. One approach is to use advanced battery management systems that can monitor and regulate the current flow in the battery to prevent overcharging and self-discharge. These systems can also help optimize the charging and discharging cycles to extend the overall lifespan of the battery.In addition, researchers are exploring ways to enhance the electrodes and electrolytes in lithium-ion batteries to reduce the feedback current and improve the overall efficiency of the battery. By using new materials and designs, it is possible tominimize the impact of feedback current on battery performance and safety.Overall, feedback current in lithium-ion batteries is a complex issue that requires careful monitoring and control to ensure the safe and efficient operation of electronic devices and electric vehicles. By investing in research and development to improve battery technology, manufacturers can continue to innovate and create more reliable and sustainable energy storage solutions for the future.。

翻译1

一种新的制备Sn-C/LiFe0.1Co0.9PO4液态的锂离子全电池的方法。

摘要：在这项工作中,我们所提出的锂离子电池使用的阴极是以Fe取代LiCoPO4做为涂层的C，阳极是纳米结构的Sn-C，电解液是以N-丁基-N-甲基吡咯-烷氧基锂-双三氟甲烷磺酰亚胺锂不易燃材料为基础介质。

初步结果表明,电池电压约为4.5 V,由于电化学嵌入/脱嵌过程取决于Co3+/Co2+氧化还原电对在阴极的反应和Li-Sn-C在阳极的合金化与去合金化过程,所以容量与特定的容量接近，为90mAh g-1。

正文：由于LiCoPO4橄榄石高电势(例如Li/Li+，4.8V)和大的理论容量（约为167mAh g-1），所以他的出现使阴极锂离子电池有了新的前途。

然而低的电子电导率和锂离子迁移率低的晶格形式仍然限制LiCoPO4实际应用[2 - 4]。

碳涂层和金属掺杂已经被提议作为合适的方法来提高橄榄石阴极的电子和离子电导率[5]。

特别是,添加小数量的Fe的LiCoPO4会大大改善锂电池的电化学性能[6、7]。

传统电解质低的电化学稳定仍然是阻碍阴极高压工作的关键。

事实上,在高压电极工作时这种电解质的分解会导致容量的快速下降。

特别是,氟化物杂质的存在,例如微量的HF,比如在使用LiCoPO4电极时，以LiPF6为基础成分电解质可以诱导电池的进一步衰退,这是由于F 阴离子的亲核攻击使得橄榄石上的P原子脱锂(带电)[8]。

这些问题中,除了由于易挥发和易燃有机烷基、碳酸盐岩存在于常见的电解质而导致安全问题可能成功地制约了使用高度稳定之外,电解液中存在的氟离子也会决定电池的电化学稳定性。

但是,非液态电解质的使用可能在常见的石墨阳极锂离子电池使用中引起一些问题,比如结构分层不稳定的固态电解质界面(S EI)的薄膜,从而导致电池不能工作[12]。

这个问题能否有效解决决定新一代的阳极的使用,例如以高容量和非凡的稳定性为表征的锂金属合金化合物等。

锂电池外文文献阅读笔记

NO.1可作为锂离子电池负极材料的PEO辅助静电硅-石墨烯复合材料
NO.2在聚丙烯腈类碳纳米纤维上使用石墨烯通过电纺技术制备二氧化硅纳米粒子
NO.3高性能锂离子电池氧化镍/镍纳米结构电极的结构设计
NO.4 NaOH表面蚀刻增强锂离子电池氧化硅阳极循环性能及其反应机理
NO.5从氰配位聚合物派生的三维微孔的Sn-Ni @ C网：迈向高性能锂蓄电池负极材料
NO.6 PH值驱动的溶解-沉淀法：一种制备新型的朝着泡沫镍上氢氧化镍纳米片阵列超薄化的超高容量锂离子电池无粘结剂阳极材料的方法
NO.7垂直排序Ni3Si2/Si纳米棒阵列作为高性能锂离子电池负极材料的研究
NO.8锂离子电池负极材料的硅纳米颗粒之间工程空空间
NO.9在聚丙烯腈类碳纳米纤维上使用石墨烯通过电纺技术制备二氧化硅纳米粒子
下面是中文文献
NO.1 Sn-Ni-Al 合金作为锂离子电池负极材料的研究
NO.2芯壳结构碳包覆二氧化锡纳米纤维膜制备及表征
NO.3锂离子电池锡基负极材料的研究进展
NO.4锂离子电池锡基复合负极材料的研究进展。

锂电池读书笔记1

一、锂电池发展过程
锂在已知金属中原子量最小，标准电极电位最负，与适当的正极材料匹配可构成高能电池。20世纪60年代开始锂电池的研究受到重视。 70年代Li/MnO2和Li/CFx等锂原电池实现了商品化，与传统的原电池相比，具有明显的优点，成为新一代高能电池。
锂二次电池的研究始于20世纪60、70年代，当时主要集中在以金属锂及其合金为负极的锂二次电池体系，正极采用的是过渡金属硫化物和过渡金属氧化物。如：Exxon公司的Li/TiS2体系，但这些电池最终亦未能实现商品化，主要原因：充电时，由于锂的不均匀沉积，电极表面易形成锂枝晶，穿过隔膜使正极与负极短路，以及金属锂较活泼，容易与电解液发生反应，由此导致的电池性能衰减和安全性问题难于解决。
电解液的侵润性
足够的吸液保湿能力
足够的离子导电性
高循环次数
力学性能和防震能力
防止外力或者是电极枝晶使隔膜破裂
寿命长
自动关断保护性能好
温度升高时自动闭孔
安全性能好
隔膜材料分为：多孔聚合物薄膜（如聚丙烯PP，聚乙烯PE，PP/PE/PP膜）、无纺布（玻璃纤维无纺布、合成纤维无纺布、陶瓷纤维纸等）、高空隙纳米纤维膜、Separion隔膜、聚合物电解质。
锂离子电池读书笔记
锂离子电池是锂电池发展而来。所以在介绍锂离子电池之前，先介绍锂电池。举例来讲，以前照相机里用的扣式电池就属于锂电池。锂电池的正极材料是二氧化锰或亚硫酰氯，负极是锂。电池组装完后电池即有电压，不需充电。这种电池也可以充电，但循环性能不好，在充放电过程中容易形成锂结晶，造成电池内部短路，所以一般情况下这种电池是禁止充电的。
正极：聚合物正极、FeS2、硒化物(NbSe3)、LiCoO2、LiNiO2、锰的氧化物
电解液：聚合物电解质、增塑的聚合物电解质

锂电池文献一篇

Solid State lonics 22 (1987) 337-344 North-Holland, Amsterdam
LITHIUM ELECTROCHEMICAL CELLS AT LOW VOLTAGE: DECOMPOSITION OF MO AND W DICHALCOGENIDES L.S. SELWYN, W.R. McKINNON, U. von SACKEN and C.A. JONES * Solid SIale Chemistry, Division of Chemistry, National Research Council of Canada, Ottawa, Canada KIA OR9
Байду номын сангаас
* NRC coop student. Present address: Department of Physics. Simon Fraser IJnivcrsity, Burnaby, British Columbia V5A lS6.
338
L.S. Selwyn et aLlLithium electrochemical cells at low voltage Moo3 (about 5 mg). Similarly, crystalline WS was made by adding 5 mg of iodine per cubic cm o P tube volume to the elements before reacting the materials at 950°C for 2 days. The materials were all single-phase as determined by x-ray powder diffraction. The two polytypes of MoTe2 also contained a small amount of Te. Ni-filtered Cu Ka radiation and a Stoe Bragg-Brentano powder diffractometer were used to obtain the diffraction data. and the lattice parameters were determined by least squares refinement of the peak positions. The lattice parameters are listed in Table 1 and agree with values compiled in [Q Cathodes of these layered materials were prepared on nickel foil and used with lithium metal anodes in electrochemical cells as described in 1103. The electrodes were separated by porous polypropylene film soaked in an electrolyte of 1M LiAsF6 (USS AgriChemicals) in distilled propylene carbonate. These cells were discharged and charged at constant current at 28.0 -rO.l”C, and the voltage monitored as a funrtion of time. Here we refer to a constant current setting that corresponds to a transfer of AT 1 lithium per MX in 10 hours as a 10 h rate. Tl e results from electrochemical cells are presented as plots of cell voltage V versus lithium content z in LirMX2 as well as plots of the inverse derivative (cYzic?I’)~ plotted versus I’. Plateaus in V(I) give rise to peaks in p(t?z,/aV), so these derivative plots are useful for displaying details not easily seen in plots of 1’ versus r. Electrically isolated cathode particles and side reartions of lithium with the electrolyte make it difficult to determine quantitatively the amount of lithium transferred to the host. We have not tried to correct for these problems; the r values shown in the V versus I

外文翻译关于锂电池

高性能锂电池阳极使用硅纳米线现代人们越来越热衷于研究大容量、长寿命的可在充电的锂电池，这些锂电池应用于便携式电子产品、电动车以及植入式医疗器械等领域。

目前，硅元素因为它的相对低的放电电压和已知的最大理论充电电压（4200mA）而被广泛应用于锂电池阳极的制作材料。

虽然硅的可再充电次数只比目前石墨材料的阳极多十几倍，比其他氧化物和各种氮化物材料的阳极多得多，但是硅阳极也只是有限应用而已，原因是硅在插入和抽出锂的过程中体积将膨胀4倍以上，导致硅效能大幅降低。

这里，我们设计一种硅纳米线电池电极绕行的方法，使得它们能够适应大应变而不至大幅降低效能，还提供一种好的物理接触和传导，并且嵌入锂中的距离短。

我们让硅阳极获得了理论上的充电容量并且最大限度的使放电容量维持在75%而让充放电循环中的损失最小。

通过以往对散装硅薄膜和微米级别的硅材料的研究中发现，锂电池的电极因使用中性能减弱、寿命短的原因归结于电极材料失效和电极中活性物质与集电器的有效接触变少。

利用微米单位的底座，微米或纳米复合材料的阳极，结果也是局限的改进。

虽然用硅薄膜做成的阳极在多个周期内都有稳定的容量，但是没有足够多的用于电池。

（如今使用单面纳米材料的理念和碳材料、Co3O4、SnO2、TiO2被用作阳极是已经被证明可行的），并且相比与散装材料性能有了提高。

纳米线直接安置在金属集流板上，这种几何学放置方式具有几个优点，而这将会在速度上改善金属氧化物阴极材料活性。

第一，本来那些在散装或微米级的材料中会发生的状况，在使用小直径的硅纳米线下可以在没有引发断裂的情况下允许更佳的适应大电流的改变，这与先前的研究一致，那个研究提出了在依赖材料的终端粒度下不会进一步的断裂。

第二，每一个硅纳米线是电连接到金属集流板，以便所有的纳米线促成容积保持。

第三，硅纳米线允许直接连通电子通路提高电荷传输效率。

在基于粒子电极微观结构下、电子载流子移动必须通过小颗粒间接触区域。

此外，每一个硅纳米线都被连接到导电电极，使对粘贴剂和导电添加剂的需要消除了额外质量。

毕业设计--锂电池的发展过程简介相关文献翻译(中文+英文)

锂电池发展简介锂离子电池是一种充电电池，它主要依靠锂离子在正极和负极之间移动来工作。

在充放电过程中，Li+ 在两个电极之间往返嵌入和脱嵌：充电池时，Li+从正极脱嵌，经过电解质嵌入负极，负极处于富锂状态；放电时则相反。

一般采用含有锂元素的材料作为电极的电池，是现代高性能电池的代表。

发展历史早期锂电池锂离子电池(Li-ion Batteries)是锂电池发展而来。

所以在介绍Li-ion之前，先介绍锂电池。

举例来讲，以前照相机里用的扣式电池就属于锂电池。

锂电池的正极材料是二氧化锰或亚硫酰氯，负极是锂。

电池组装完成后电池即有电压不需充电。

这种电池也可以充电，但循环性能不好，在充放电循环过程中容易形成锂结晶，造成电池内部短路，所以一般情况下这种电池是禁止充电的。

[2] 炭材料锂电池后来，日本索尼公司发明了以炭材料为负极，以含锂的化合物作正极的锂电池，在充放电过程中，没有金属锂存在，只有锂离子，这就是锂离子电池。

摇椅式电池我们通常所说的电池容量指的就是放电容量。

在Li-ion的充放电过程中，锂离子处于从正极→负极→正极的运动状态。

Li-ion Batteries就像一把摇椅，摇椅的两端为电池的两极，而锂离子就象运动员一样在摇椅来回奔跑。

所以Li-ion Batteries又叫摇椅式电池。

发展时间点1970年代埃克森的M.S.Whittingham采用硫化钛作为正极材料，金属锂作为负极材料，制成首个锂电池。

1982年伊利诺伊理工大学(the Illinois Institute of Technology)的R.R.Agarwal和J.R.Selman发现锂离子具有嵌入石墨的特性，此过程是快速的，并且可逆。

与此同时，采用金属锂制成的锂电池，其安全隐患备受关注，因此人们尝试利用锂离子嵌入石墨的特性制作充电电池。

首个可用的锂离子石墨电极由贝尔实验室试制成功。

1983年M.Thackeray、J.Goodenough等人发现锰尖晶石是优良的正极材料，具有低价、稳定和优良的导电、导锂性能。

软包锂电池英文文献

软包锂电池英文文献Soft-Packed Lithium-Ion Batteries: A Technical Overview.Lithium-ion batteries (LIBs) have revolutionized theway we power our electronic devices, with their high energy density, low self-discharge rate, and long cycle life. Among various battery configurations, soft-packed lithium-ion batteries (SPLBs) have emerged as a popular choice fora wide range of applications, thanks to their unique advantages.Advantages of Soft-Packed Lithium-Ion Batteries.SPLBs offer several advantages compared to traditional battery formats. Firstly, their flexible packaging allowsfor a more compact and lightweight design, making them suitable for space-constrained applications. Secondly, the soft packaging material enhances the battery's safety by preventing internal short circuits and mitigating theimpact of external forces. Furthermore, SPLBs offer betterheat dissipation, enabling them to operate at higher temperatures without compromising performance.Construction and Materials Used.Soft-packed lithium-ion batteries are constructed using a combination of aluminum and plastic films as the outer packaging. This packaging material is chosen for its excellent strength, flexibility, and insulating properties. Inside, the battery comprises an anode, a cathode, a separator, and an electrolyte. The choice of materials for these components is crucial for the battery's performance and safety.Working Principles.During discharge, lithium ions move from the anode, through the separator, to the cathode. This process generates electricity, which powers the connected device. During charge, the ions flow in the opposite direction, returning to the anode. The separator ensures that the ions move through the battery safely, preventing direct contactbetween the anode and cathode, which could lead to short circuits.Applications.Soft-packed lithium-ion batteries are widely used in consumer electronics, electric vehicles, and renewable energy systems. In consumer electronics, their lightweight and compact design makes them ideal for portable devices like smartphones, laptops, and wearables. In electric vehicles, SPLBs offer high energy density and fast charging capabilities, enabling longer driving ranges and shorter charging times. In renewable energy systems, they are used to store energy generated by solar panels or wind turbines, ensuring a continuous supply of power even when the weather conditions are not favorable.Challenges and Future Developments.Despite their many advantages, SPLBs face some challenges, such as safety concerns and recycling issues. Ongoing research is focused on developing safer batterychemistries, improving their thermal stability, and enhancing their recycling potential. Future developments in SPLB technology could lead to even higher energy densities, faster charging speeds, and improved lifespans.Conclusion.Soft-packed lithium-ion batteries represent asignificant advancement in battery technology, offering unique advantages in terms of compactness, lightweight design, and safety. Their widespread use in consumer electronics, electric vehicles, and renewable energy systems underscores their importance in powering our modern, mobile world. As research continues to address the challenges associated with SPLBs, we can expect further improvements in their performance and safety, enabling even more innovative applications in the future.。

锂电池的英语介绍作文

锂电池的英语介绍作文Lithium battery is a kind of battery which uses lithium metal or lithium alloy as positive electrode material and non-aqueous electrolyte solution. The earliest lithium battery came from the great inventor Edison, who used the following reaction: Li + MnO2 = LiMnO2 this reaction is anoxidation-reduction reaction and discharge. Because the chemical characteristics of lithium metal are very active, the processing, storage and use of lithium metal have very high environmental requirements. Therefore, lithium batteries have not been used for a long time. Now lithium battery has become the mainstream.Lithium battery refers to a battery containing lithium (including metal lithium, lithium alloy, lithium ion and lithium polymer) in an electrochemical system. Lithium batteries can be broadly divided into two categories: lithium metal batteries and lithium ion batteries. Lithium ion batteries do not contain metallic lithium and are rechargeable. Lithium metal battery, the fifth generation product of rechargeable battery, was born in 1996. Its safety, specific capacity, self discharge rate and performance price ratio are better than lithium ion battery. Due to its own high-techrequirements, only a few companies in several countries are producing such lithium metal batteries锂电池是一类由锂金属或锂合金为正极材料、使用非水电解质溶液的电池。

锂离子电池容量衰减机理和副反应-翻译(个人翻译的外文文献)

锂离子电池容量衰减机理和副反应-翻译(个人翻译的外文文献)Capacity Fade Mechanisms and Side Reactions inLithium-Ion Batteries锂离子电池容量衰减机机理和副反应Pankaj Arorat and Ralph E. White*作者：Pankaj Arorat and Ralph E. White*Center For Electrochemical Engineering, Department of Chemical Engineering, University of South Carolina,Columbia, South Carolina 29208, USA美国，南卡罗来纳，年哥伦比亚29208，南卡罗来纳大学，化学工程系，中心电化学工程ABSTRACT 摘要The capacity of a lithium-ion battery decreases 锂离子电池容量随着循环during cycling. This capacity loss or fade occurs due to 衰减。

容量损失或者衰减的发several different mechanisms which are due to or are 生主要是由于以下几种反应机associated with unwanted side reactions that occur in these 理，这些机理起因于或者关联batteries. These reactions occur during overcharge or 于一些我们不希望发生在电池overdischarge and cause electrolyte decomposition, passive 里的副反应。

这些反应发生在filmformation, active material dissolution, and other 过充或者过放中，导致了电解phenomena. These capacity loss mechanisms are not 液分解、钝化膜的形成、活性included in the present lithium-ion battery mathematical 物质溶解和其他现象形成。

锂电池-lithium ion battery-能源存储-energy storage

Energy storageLithium ion battery is the power source of modern electric vehicles and is a device converting chemical energy into electrical energy. These days everyone hears of lithium ion batteries, but what makes them so special? Comparing to the other energy storage devices, lithium ion battery has the longest life and specific energy density. How to further improve the energy density of lithium ion batteries? There are three main factors contributing to the energy density, which are working voltage, theoretical capacity and less inactive substance.First of all, working voltage is a key parameter measuring the properties of a battery as we know that the energy density of a battery can be approximately calculated with a formula: Energy=V oltage*Capacity. With higher working voltage, we can get higher energy density.Secondly, theoretical capacity is another important factor which influences the energy density of a battery. According to paragraph two, we can know capacity is equally the same importance with working voltage on improving the energy density of a battery. With higher theoretical capacity, higher energy density will be acquired. These days, researchers are trying to develop silicon anode in order to substitute the temporary graphite anode as we can see silicon has a theoretical capacity of 4200mAh/g, which is more than ten times higher comparing to graphite anode, which only has a theoretical capacity of 372mAh/g.Finally, to reduce the inactive substance is very importance in improving the energy of a battery as we know that a battery consists of many components, mainly including cathode, anode, separator, electrolyte and packing materials. Only the cathode and anode can store the energy, to further improve the energy density of a battery, we get to use thinner separator, less electrolyte and lighter packing materials.In conclusion, working voltage, theoretical capacity and inactive substance are the three main factors that influence the energy density of a battery, in order to acquire higher energy density, we need to pay more attention in finding new electrode materials and try to reduce the thickness of a separator and use as less inactive substance as possible.。

锂电池外文资料译文

The design of the lithium battery charger IntroductionLi-Ion rechargeable batteries are finding their way into many applications due to their size, weight and energy storage advantages.These batteries are already considered the preferred battery in portable computer applications, displacing NiMH and NiCad batteries, and cellular phones are quickly becoming the second major marketplace for Li-Ion. The reason is clear. Li-Ion batteries offer many advantages to the end consumer. In portable computers,Li-Ion battery packs offer longer run times over NiCad and NiMH packs for the same form factor and size, while reducing weight. The same advantages are true for cellular phones. A phone can be made smaller and lighter using Li-Ion batteries without sacrificing run time. As Li-Ion battery costs come down, even more applications will switch to this lighter and smaller technology. Market trends show a continual growth in all rechargeable battery types as consumers continue to demand the convenience of portability. Market data for 1997 shows that approximately 200 million cells of Li-Ion will be shipped, compared to 600 million cells of NiMH. However, it is important to note that three cells of NiMH are equivalent to one Li-Ion cell when packaged into a battery pack. Thus, the actual volume is very close to the same for both. 1997 also marked the first year Li-Ion was the battery type used in the majority of portable computers, displacing NiMH for the top spot. Data for the cellular market showed a shift to Li-Ion in the majority of phones sold in 1997 in Europe and Japan.Li-Ion batteries are an exciting battery technology that must be watched. To make sense of these new batteries, this design guide explains the fundamentals, the charging requirements andthe circuits to meet these requirements.Along with more and more the emergence of the handheld electric appliances, to the high performance, baby size, weight need of the light battery charger also more Come more big.The battery is technical to progress to also request continuously to refresh the calculate way more complicatedly is fast with the realization, safety of refresh.Therefore need Want to carry on the more accurate supervision towards refreshing the process, to shorten to refresh time and attain the biggest battery capacity, and prevent°from the batteryBad.The AVR has already led the one step in the competition, is prove is perfect control chip of the next generation charger. The microprocessor of Atmel AVR is current and can provide Flash, EEPROM and 10 ADCses by single slice on the market Of 8 RISC microprocessors of the tallest effect.Because the saving machine of procedure is a Flash, therefore can need not elephant MASK ROM Similar, have a few software editions a few model numbers of stock.The Flash can carry on again to weave the distance before deliver goods, or in the PCB Stick after pack carry on weaving the distance throughan ISP again, thus allow to carry on the software renewal in the last one minute.The EEPROM can used for conservancy mark certainly coefficient and the battery characteristic parameter, such as the conservancy refreshes record with the battery that raise the actual usage Capacity.10 A/ Ds conversion machine can provide the enough diagraph accuracy, making the capacity of the good empress even near to its biggest capacity. And other project for attaining this purpose, possible demand the ADC of the exterior, not only take up the space of PCB, but also raised the system Cost.The AVR is thus deluxe language but 8 microprocessors of the designs of unique needle object" C" currently.The AT90S4433 reference The design is with" C" to write, the elucidation carries on the software design's is what and simple with the deluxe language.Code of C this design is very Carry on adjust easily to suit current and future battery.But the ATtiny15 reference design then use edit collected materials the language to write of, with Acquire the biggest code density.An electric appliances of the modern consumption mainly uses as follows four kinds of batteries:1.Seal completely the sour battery of lead( SLA)2.The battery of NiCd3.The NiMHhydrogen battery( NiMH)4.Lithium battery( Li- Ion)At right choice battery and refresh the calculate way need to understand the background knowledge of these batteries. Seal completely the sour battery( SLA) of lead seals completely the sour battery of lead to mainly used for the more important situation of the cost ratio space and weights, such as the UPS and report to the police the backup battery of the system. The battery of SLA settles the electric voltage to carry on , assist limits to avoid with the electric current at refresh the process of early battery lead the heat.Want ～only the electricity .The pond unit electric voltage does not exceed the provision( the typical model is worth for the 2.2 Vs) of produce the company, the battery of SLA can refresh without limit. The battery of NiCd battery of NiCd use very widespread currently.Its advantage is an opposite cheapness, being easy to the usage;Weakness is from turn on electricity the rate higher.The battery of NiCd of the typical model can refresh 1,000 times.The expired mechanism mainly is a pole to turn over.The first in the battery pack drive over.The unit that all turn on electricity will take place the reversal.For prevent°froming damage the battery wrap, needing to supervise and control the electric voltage without a break.Once unit electric voltage Descend the 1.0 Vs must shut down.The battery of NiCd carries on refresh in settling the electric current by forever . The NiMH hydrogen battery( NiMH) holds to shoot the elephant machine such as the cellular phone, hand in the hand that the importance measure hold equipments, the etc. NiMHhydrogen battery is anusage the most wide.This kind of battery permit.The quantity is bigger than NiCd's.Because lead to refresh and will result in battery of NiMH lose efficacy, carry on measuring by the square in refresh process with.Stop is count for much in fit time.Similar to battery of NiCd, the pole turn over the battery also will damage.Battery of NiMH of from turn on electricity the rate and is probably 20%/ month.Similar to battery of NiCd, the battery of NiMH also settles the electric current to refresh .Other batteries says compare in lithium battery( Li- Ion) and this texts, the lithium battery has the tallest energy/ weight to compare to compare with energy/ physical volume.Lithium batterySettle the electric voltage to carry on refresh with , want to have the electric current restrict to lead the heat in the early battery of refresh the process by avoid at the same time.When refresh the electric current Descend to produce the minimum electric current of the enactment of company will stop refresh.Leading to refresh will result in battery damage, even exploding.The safety of the battery refreshes the fast charge machine( namely battery can at small be filled with the electricity in 3 hours, is usually a hour) demand of the modern.Can to the unit electric voltage, refresh the electric current and the battery temperatures to carry on to measure by the square, avoid at the time of being filled with the electricity because of leading to refresh.Result in of damage.Refresh the method SLA battery and lithium batteries refreshes the method to settle the electric voltage method to want to limit to flow for the ever ; The battery of NiCd and battery of NiMHs refresh the method.Settle the electric current method for the ever , and have severals to stop the judgment method for refresh differently. Biggest refresh the electric current biggest refresh the electric current to have relation with battery capacity( C).Biggest usually refresh the electric current to mean with the number of the battery capacity.For example,The capacity of the battery for 750 mAhs, refresh the electric current as 750 mAs, then refresh the electric current as 1 C(1 times battery capacity).IfThe electric current to flow refresh is a C/40, then refreshing the electric current for the battery capacity in addition to with 40.Lead the hot battery refresh is the process that the electric power delivers the battery.Energy by chemical reaction conservancy come down.But is not all.The electric powers all convert for the sake of the chemistry in the battery ability.Some electric power conversions became the thermal energy, having the function of the heating to the battery.When electricity.After pond be filled with, if continue to refresh, then all electric powers conversion is the thermal energy of the battery.At fast charge this will make the battery.Heat quickly, if the hour of can not compare with stop refresh and then willresult in battery damage.Therefore, while design the battery charger, to the temperature.It is count for much that carry on the supervision combine to stop refresh in time.The discretion method battery stopped refresh of different and applied situation and work environment limitted to the choice of the method that the judgment stop refresh.The sometimes temperature allow of no.Measure easily, but can measure electric voltage, or is other circumstances.This text takes the electric voltage variety rate(- dV/ dt) as the basic judgment to stopThe method for refresh, but with the temperature and absolute electric voltage be worth for assistance and backup.But the hardware support that this text describe speaks as follows.The method of the havings of say. Time of t – this method that is the decision when stop refresh most in ually used for spare project of the hour of fast charge.Sometimes also be .Refresh(14- 16 Hour) basic project of the method.Be applicable to various battery.Stop refresh when the electric voltage of V – be the electric voltage to outrun the upper ually with the forever settle the electric current refreshes the match usage.The biggest electric current is decide by the battery, usually For the 1 C.For prevent°froming refresh the electric current leads to causes battery lead greatly hot, the restrict of the electric current at this time very key.This method Is a lithium battery basic to refresh and stop project. The actual lithium battery charger usually still continues into after attain biggest electric voltage Go the second stage refresh, to attain 100% battery capacity. For battery of NiCd and battery of NiMHs are originally method can Be the spare judgment stops refreshing the project. - The method exploitation that this judgment of the dV/ dt – electric voltage variety rate stops refresh negative electric voltage variety rate.For the battery of some types, be the battery to be filled with the subsequence Refreshing continuously will cause electric voltage descend. At this time this project was very fit.This method usually useds for the ever to settle the electric current to refresh, Be applicable to to the fast charge of the battery of NiCd and battery of NiMH. The electric current of I –is to refresh the electric current small in a certain the number that set in advance stop refresh. Usually used for the ever to settle the electric voltage to refresh the method.Be applicable to the SLA Battery and lithium battery.The T – temperature absolute zero can be the basis that battery of NiCd and battery of NiMHs stop refresh, but even suited for to be the backup project.Any battery for temperature to outrun initial value have to stop refresh.The basis that the dT/ dt –temperature rising velocity fast charge variety rate of the temperature of hour can be to stop refresh.Please consult the norm that the battery produces the company( battery of NiCdOf typical model be worth for the 1 oC/ min) the –be applicable to the battery of NiCd and battery of NiMHs.Need to stop refresh when the DT – outrun the temperature value of theenvironment temperature to be the bad battery temperature and the environment temperature to exceed the certain threshold.This method can be the battery of NiCd and The project that battery of SLA stops refresh.While refreshing in the cold environment this method compares the absolute zero to judge the method better.Because bigMost systems usually only have a temperature to stretch forward, have to will refresh the previous temperature to be the environment temperature. DV/ dt=0 –s zero electric voltages differ this method with- the method of dV/ dt is very and similar, and more accurate under the condition that electric voltage will not go up again. Be applicable to the NiCd Battery and battery of NiMH.This reference design completely carried out the battery charger design of latest technique, can carry on to various popular battery type quicklyRefresh but need not to modify the hardware soon, a hardware terrace carries out a charger product line of integrity.Need only Want to will refresh the calculate way to pass lately the ISP downloads the processor of FLASH saving machine can get the new model number.Show very muchHowever, this kind of method can shorten time that new product appear on market consumedly, and need a kind of hardware of stock only.This design provide The in keeping with SLA, NiCd, NiMH of the integrity and the database function of the battery of Li- Ion.锂电池充电器的设计介绍根据其尺寸，重量和能量储存优点，锂- 离子可再充电电池正在被用于许多的应用领域。

锂离子电池英文资料

锂离子电池英文资料锂离子电池技术英文词句2.3 assembly line process(5/15)流水线工艺film loading-vacuum on-film folding-sliding jig backward-top cutting-sliding jig forward-vacuum off-film unloading放上包装膜—抽真空—包装膜折叠-分切夹心的后端-剪掉顶部-分切夹心的前段-释放真空-拿下包装膜station 岗位two station 两个岗位folding 折叠guide type 指导方式top cutting 顶部剪切knife 刀片2.3 assembly line process(6/15)流水线工艺j/r loading-vacuum on-j/r jig backward-bottom former up-upper former down-放极组-抽真空-极组夹具放在后端-模板末端在上面-顶端在下面- heating forming-former up,down-j/r jig forward-vacuum off-j/r unloading加热模板-模板上下翻转-极组夹具朝前-释放真空-取下极组station two station岗位两个岗位heating forming pressing time,preset timer加热模板施压时间施压次数temperature thermocouple温度热电耦time:mmin,2~max.3sec时间：press force :40~50kg压力temperature:150℃温度2.3 assembly line process(7/15)流水线工艺film loading-fim clamp-sliding jig backward-edge pushing-tab clamp-tab unclamp-放上包装膜-包装夹具-分切极组末端-整边-放极耳夹具-卸下极耳夹具sliding jig forward-cell unloading分切极耳前端station two stationheat sealing top热封sealing thickness control(micrometer)热封厚度控制（毫米）sealing control pressing time,preset timer热封控制施压时间施压次数precision regulator精度校准temperature, thermocouple温度热电耦time :min.2~max.3sec时间press force:250kg压力temperature:180~250℃温度2.3 assembly line process(9/15)流水线工艺cell loading-vacuum on-sliding jig backward-side cutting-feeding-tab cutting-放上电芯-抽真空-滑动夹心后端-裁边-流入下工序-剪极耳sliding jig forward-cacuum off-cell unloaing滑动夹心前端-释放真空-取下电芯station two stationside cutting knifeside cutting force 100kgtab cutting knifetab cutting force 100kg2.3 assembly line process(10/15)流水线工艺cell loading-sliding jig backward-vacuum pad down-open-needle down-e/l filling(e/l-needle up-needle up-vacuum pad up-sliding jig forward-cell unloadingstation two statione/l supply 3kuter sub-tank on equipmentmetering pump hi -bar pump,hbd-2bc-17accuracy; under 3.0;±0.1gocer 3.0; ±3.5g2.3 assembly line process(11/15)流水线工艺cell loading-sliding jig backward-jig backward-jig up-vacuum(vacuum chamber)-放上电芯-滑动夹心后端-夹心向后-再向上-抽真空-sealing block forward-sealing热封前端- 密封--sealing block backward-jig down-silding jig forward-cell loading-formation热封后端- 夹心翻转向下-滑动夹心前端-取下电芯-成型station two stationvacuum source 740mmhg max.vacuum pumpsealing control pressing time preset tiomerpressing force, precision regulatortemperature, thermocouple热电偶time:min.3~max4secpress force:250kgtemperatrure:180~250℃2.3 assembly line process(12/15)流水线工艺cell loading-conveyor drive-numbering-numbering-head down-vacuum on-放上电芯- 启动传送带- 编号码-编号码-电芯朝下-抽真空head up-head forwward-head down-vacuum purge-head up-cell unloading电芯朝上- 电芯朝前- 电芯朝下-真空净化- 电芯朝上-取下电芯speed controller motor 25Wnumbering ink jet printercell unloading magacine2.3 assembly line process(13/15)流水线工艺piercing-cell loading-sliding jig backward-jig up-vacuum&degassing-穿透？？- 放电芯-滑动夹心后端-夹心向上- 抽真空&脱气sealing block forward-sealing-sealing block backward-jig down-sliding jig forward-cell loading热封前端- 热封–热封后端-滑动夹心前端–取电芯station two stationpiercing ∮6holevacuum source 750mmhg max.vacuum pumpsealing comtrol pressing time ,preset timerpressing force,preision regulator调整压力temperature,thermocouple(温度热电偶)time: min.3~max.4sec时间press force:250kg(压力)temperature:180~250℃(温度)2.3 assembly line process(14/15)流水线工艺cell loading-vacuum on-sliding jig backward-cutter down-cutting-cutter up-放电芯-抽真空-滑动夹心后端-切割刀具向下-切割-切割刀具向上sliding jig forward-vacuum off-cell loading滑动夹心前端- 释放真空-取下电芯电池封口--cutting(切断) knife(刀)2.3 assembly line process(15/15)流水线工艺cell loading-ist folding-2nd folding-heat pressing-3nd folding-4th folding(sicing)放电芯- 第一次折叠-第二次折叠-热压-第三次折叠-第四次折叠cell unloading取下电芯manual-loading-2st foliding-heat pressing-3nd folding-4th folding手工–放上- 第二次折叠- 热压- 第三次折叠- 第四次折叠cell transfer linear transferfolding actuator pneumatic actuatorheat pressing pressing time,preset timerpressing forceprecision regulatortemperature, thermocoupletime:min.2~max.3 secpress force:40kgtemperatrure:80~100℃2.3 assembly line process(1/6)流水线工艺jelly roll supply-jelly roll loading-cell alignment-tab straightening-提供极组-放上极组-电芯排列好-将极耳伸直sealant sealing(sealant film supply)-sealant sealing(sealant film supply)-final sealing- 密封胶密封（密封膜供给）-密封胶密封（密封膜供给）-最终的密封sealant film check-tab forming-jelly roll unloading(ng unloading)检验密封膜-极耳成型-取下极组2.3 assembly line process(2/6)流水线工艺al-foil supply-pre heating(contact)-pouch forming---pouch punch out-—供应箔（铝塑膜）-预热（连接）-成型成袋状- 袋状膜冲压打孔pouch loading(pouch pin hole check)-pouch loading-ist folding-lst folding-2nd folding- 放上袋状膜（检验针孔）-放上袋状膜- 第一次折叠-第二次折叠top cutting(ng unloading)-jelly roll insertion(jelly roll alignment-jelly roll loading)—剪掉顶部—插入极组（调整极组-放上极组）3nd folding-pre heat sealing-package unloading第三次折叠-预热密封—取下包好的电芯2.3 assembly line process(3/6)流水线工艺cell loading-lst top sealing--2nd top sealing-top cooling-side sealing-side cooling-放上电芯-第一次顶部密封-第二次顶部密封-顶部冷却—封边—两边冷却side cutting-short check-cell unloading-ng unloading裁边- 测短路—取下电芯—ng是什么啊package loading-pre weighing-package opening-e/l filling(e/l dispensing e/l supply tank) 放上包装好的电芯—预称重—打开电芯--- 注液（分配电解液电解液供给罐）--lst vacuum-2nd vacuum --lst sealing-2nd sealing-plst-weighing-package unloading-第一次抽真空---第二次真空---第一次密封---第二次密封------称重---取下电芯package loading-package aging--formation 放上电芯---电芯老化-----化成cell loader-cell-loading-piercing-vacuum&degassing heat sealing-2nd sealing-装电芯设备-电芯-装上电芯—穿透（？？）-抽真空& 脱气热封—第二次密封side trimming-cell unloading修边--- 取下电芯cell loading-lst folding-2nd folding-3rd folding-4th folding-5th folding(sizing)-放电芯---第一次折叠---第二次折叠---第三次折叠---第四次折叠---第五次折叠（量尺寸）5th folding(sizing)-tab cutting-height&vision check-final weighging-final weighting- 第五次折叠（量尺寸）---剪极耳---检验高度&视觉---最后称重ng rejection-cell unloading-cell unloading-cell palleticing挑选，排除---取下电芯--- （用托盘）搬运电芯1.1 assembly line specification –products流水线特殊产品can type(壳体类型) aluminum can(A3003) 铝壳（材质A3003）conventional prismatic type ,not oval type 传统的方型，不是椭圆型model of cell电池型号basic design model:xx-yy—zz基本设计型号：XX-YY-ZZ range 范围w:30~34mm t:4.0 ~10mm h:40~67mm宽：厚：高：cathode tab正极耳AL,t0.08~0.12mm,w3/4mm铝带，厚度0.08~0.12mm宽度3/4mm welding to top cap with ultrasonic welder 用超声波焊接机超焊在极片头部anode tab负极耳ni,t0.08~0.12mm,w3/4mm镍带，厚度0.08~0.12mm宽度3/4mm welding to top cap with resistance spot welder用阻抗点焊机焊在极片头部can seam welding壳盖的缝隙焊接side welding侧面焊接top insulator 顶部绝缘片injection molded注液模具bottom tape wrapping底部贴胶纸pp-tape,same as j/r wrapping tape, roll,w:28~32mmt:0.05~0.10mm o.d:200mm core id:3inchesfor xx30zz width 28mm,for xx34zz width 32mmfill port welding 补焊砂眼AL Ball (Al050,∮1.37±0.03mm),laser seam welding 激光焊接e/l filling accuracy 精确注液量under 3.0g; ±0.1gover 3.0g ±3.5g r/l filling volume:1~7g 注液量范围1~7gmodel change exchange tool,jig, carrier&tray搬运工具，夹具，搬运盒&托盘option:only carrier&tray (others:sutomatically adiusted其它：适当调整)tray托盘jr极组(256pcs),can壳(300pcs),cap盖帽(100pcs),(rivet) all trays are prepared user1.2 assembly line specification –equipment流水线特殊设备line tact time 流水线标准工时 2.0(30ppm)Drive mechanism 发动装置cam,ac servo drive&air actuatorelectrical power 电源286kva,3p-380v±10%,50hz±1hzpneumatic source 气源13300l/min,0.6mpa (include welding jig cooling包括焊接模具冷却)nitrogen gas 氮气285 l/min, 0.6mpa(for laser welding shield gas激光焊接防护气)laser cooling water激光焊冷却水320 l/min,below25℃fume collector 烟、气收集罐400cfm,explosion-proof type for al-fume,outdoor typefume suction main piping 抽气主管道系统 4 inchexhaust piping排气管道系统5inchdry air piping干燥气管道系统5inchdry chamber(total) 干燥室20.78m3total weight总重量14.8ton(approx大概),(not include laser welder不包括激光焊接机)floor load 场地负荷1500kg/m2dry room height干燥室高度2500mm(min)can seam welding壳盖的缝隙焊接side welding侧面焊接,welding speed 焊接速率10~15mm/sec.(approx) cartesian robot stageelectrolyte filling process注电解液工序40station-80 jig index unit,vacuum真空&pressurize加压elctrolyte filling range注液范围depend on internal dead space of cell design根据电池设计内部的绝对空间hbd-2bc series of hibar pum, japan hibarleak check 测漏differential pressure check system,100pa max.不同压力测试系统，最大为100pa accuracy:+/-0.5%精确度need test actual work 需要通过实际操作测量2.1 assembly parts name&compositionball-top cap assembly盖板流水线(t/c)--top insulator顶部绝缘片(t/l)-cathode正极耳(al-tab铝带)-anode负极耳(ni-tab镍带)- bottom tape底部胶纸(b/t)-jelly roll极芯(j/r)-aluminum can铝壳2.2 assembly process basic specification装配过程概述3.1 prismatic lib assembly processbottom tape底部胶纸-jelly roll insertion极芯入壳-top insulator顶部绝缘片-tab forming极耳修整-top-cap welding顶部极耳焊接-top cap folding极耳折叠-top cap setting卡极耳-seam welding焊缝焊接-leak check测漏-electrolyte filling注液- ball insertion压钢珠-fill port welding补焊砂眼（）3.2 assembly line process(1/8)can supply供应壳non dust paper tray无尘的纸盘can tray size装壳的盘子尺寸270*212*22/32htray capacity盘子容量423048-450can/tray343450-496can/tray(suppiled by user)stack volume堆叠范围48/50h:8tray65/67h:6traycan supply供应壳体-can loading放上壳体-can check检验壳体-jelly roll loading放上极芯(ng reject-bottomtape check检验底部胶纸-bottom tape wrapping贴底部胶纸-jelly roll supply供应极芯-from winder从卷绕机)-jelly roll centering 极芯放在正中央-jelly roll insertion插入极芯-insertion height check检验极芯入壳高度-ng rejectj/r supply 极芯供应tray from winder来自卷绕机的盘子j/r tray size放极芯盘子的尺寸540*540*50hj/r capacity 容纳极芯的数量48/50h:40*8=320/tray65/67h:40*6=240/tray supplied by userstack volume堆叠范围8 traytray handling盘子搬运using manual cart用手推车bottom tape底部胶纸pp tape,rollcore size标准尺寸 3 inch paper coreb/t color 底部胶纸颜色blue or green兰色或绿色b/t check 检验底部胶纸color sensor颜色传感器3.2 assembly line process(2/8)tab straightening拉直极耳—tab position check检查极耳位置—top insulator insertion插入绝缘片(t/I escapement镊子？？—top insulator supply供应绝缘片)—T/I presence check检查绝缘片—tab forming极耳修整—j/r final insertion极芯入壳—t/c welding 盖板焊接(ni tab镍带)—(t/c direction check检查盖板方向—top cap supply盖板供应)—al tab welding铝带超焊—cap/tab welding check检验焊接是否牢固—tab folding极耳折叠—t/csetting&check固定、检验盖板—ng rejecttop cap supply盖板供应tray from cap ass’y m/ccap tray size 装盖板盘子的尺寸340*240*18hcap capacity能装盖板的数量18*6=108 cap/traystack volume 堆叠范围24 tray(2592 cap)j/r final insertion极芯入壳include j/r insertion height check 包括检验极芯入壳高度ni-tab welding焊接镍带resistance spot welding,2points阻抗点焊机，2点include welding current monitor包括焊接电流监控器al-tab welding铝带超焊ultrasonic welding超声波焊接40khx/800w/branson brandtop insulator顶部绝缘片pull check拉力测试cap height check盖板高度检验t/c setting check 检验盖板牢固性setting height check检验固定的高度3.2 assembly line process(3/8)height check#1高度检验1#—pre spot welding预点焊—height check#2高度检验2#—ng reject排除不合格品？？—seam welding#1焊缝焊接1#—seam welding#2焊缝焊接2#—seam welding#3焊缝焊接3#—seam welding#4焊缝焊接4# (jig cooling模具冷却)—short check 测短路—ng reject排除不合格品pre spot welding预点焊laser spot welder激光点焊机,3-points 50w/2-fiber,1system(supplied by user)height check#1 高度检验1# check the top cap setting height 检查盖板固定的高度height check#2 高度检验2# check the top cap welded height 检查盖板焊接高度seam welding缝隙焊接laser welder激光焊接机,10~15mm/sec,700w/2-fiber,4systemsrequire speed down for 34xxyy 对于34xxyy需减速models (prevent against overheat预防过热)supplied by user jig cooling 模具冷却vortex tube,using compressed air热交换管道，采用压缩气体air pressure 0.65mpa (minimum)气压shield gas supply保护气供应nitrogen gas,0.65mpa18/min氮气with digital flow meter数显流动仪表fume collector烟气收集罐400 cfm,1.5kw,amanl/japanexplosion proof,outdoor type户外气体排放装置short check测短路lcr meter3.2 assembly line process(4/8)vacuum out释放真空—equilibrium平衡状态—leak detection 测漏—vent排除气体—ng reject排除不合格品leak check procedure 测漏程序atmosphere气体—vacuum抽真空—equilibrium平衡状态—detection测漏—leaked cell漏气电芯—normal cell 正常电芯leak check测漏differential pressure,100pa max.. 不同压力测试系统，最大为100pavacuum out-100kpa max.释放真空leak detection time 8.0sec.max.测漏时间using master cell采用好的电芯accuracy:+-0.5%精确度cell handling搬运电芯8 cells,simultaneously check 8只电芯，同时检查3.2 assembly line process(5/8)pre weighing预称重—cell loading放上电芯—e/l dispensing 电解液分配—vacuum/vent抽真空/排气—vacuum 抽真空—pressurize加压—vent排气—cell unloading取下电芯—post weighting快速称重—ng rejectelectrolyte supply供应电解液drum桶,200 literusing nitrogen gas使用氮气, 0.02~0.04mpasub-tank in equipment装置内的储槽,3 litermetering pump 抽吸仪表hibar pump,japan hibarhbd-2bc series*2vacuum抽真空-700mmhg,(max.-740mmhg)suction capacity抽吸泵容量310/min.r5c 0040e*02,busch/germany德国？？Pressurize加压nitrogen gas氮气,0.15~0.2mpaWeighing称重load-cell,6digits,nmb/japan日本Display显示;000.00gnozzle cleaning 清洗喷嘴nitrogen gas blow out用氮气吹,0.15~0.2mpafor blow out the remained e/l 把剩余的电解液吹出来process time 工序工时128sec (max)filling accuracy 注液精确度under 3.0g;±0.1g 小于3.0g，±0.1g over 3.0g; ±3.5% 大于3.0g; ±3.5%3.2 assembly line process(8/8),al ball typecleaning paper supply供应纸巾-cap face cleaning清洁盖帽表面-cleaning paper supply供应纸巾-cap face wet cleaning盖帽表面除湿-solvent dispenser溶剂给料器-fill port cleaning清洁注液孔-cleaning paper supply供应纸巾-ball insertion钢珠插入-ball supply钢珠供应-ball press压钢珠-ball height check检验压钢珠的高度--ball seam welding钢珠缝隙焊接-welding check焊接检验-uv glue dispensing UV胶水给料-ng reject-uv curing紫外光固化-cell unloading取下电芯cleaning paper清洁纸巾non-dust paper,roll,width 14mm无尘纸巾，卷，14mm宽3 inch paper coreballsupply钢珠供应bowl feeder钢珠进料器requies testing by the actual sample目前测试样版ball press force压力35~40kgfseam welding定位焊接方法laser seam welder,6.5mm/sec激光焊接工作350w/-fiber,1 system焊接系统(supplied by user)适当调整6.1 model change time 型号变化时间manual conversion type 46-30-48 vs 46-30-xx:6 hours approx.(only different'heieght)xx-xx-xx vs yy-yy-yy:3days6.2 delivery交货manual conversion type 7months to shipping,after l/c open6.3 customer scope 客户范围primary main power wiring to control panel of the each equipment,with main power panel.主要的电源线控制每一个设备的主电路板Primary main pneumatic piping to beside the each equipment, with main air-filter unit.主要的气管道系统装在每个设备的旁边，主要的气体过滤器Primary main nitrogen gas piping to beside the each equipment, with main gas -line filter unit.主要的氮气管道系统装在每个设备的旁边，主要的气体过滤器/All duct piping for suction &exhaust from equipment's inlet/outlet to main duct.所以用于从设备上的进口/出口抽气或排气的输送管道Installation &piping/wiring/wiring for fume collector(outdoor type)给烟气收集器（户外类型）安装管道系统/配线系统Inlet/drain water piping of the washing machine,with waterstrainer.清洗设备的进水/排水管道，水过滤器Laser welding system &laser welder welder import/export fee激光焊接系统&激光输入/输出Cooling water piping for each laser system,below 25℃.(it requires a water filter (strainer)用于激光系统的冷却水，25℃以下（需要一个水过滤器）Cooler or chiller for laser cooling water.激光冷却水的冷却器Dry pneumatic piping for laser shutter operation to each laser system.用于每一个激光系统的激光开关操作的干燥气管道Installation&wiring/cabling for laser fiber and laser control cable.给激光光纤和激光控制电缆安装配线/电缆Installation &wiring/cabling for laser control pendant.给激光控制的悬吊物安装配线/电缆6.4 laser system location outdoor of the dry room. It requires air-conditioning or sufficient ventilation.激光系统位于干燥间的外面。

英语阅读理解锂离子

英语阅读理解锂离子Lithium-ion （锂离子）batteries are the current front-runners for storing renewable energy, but their components can be expensive.Zinc （锌）batteries are easier on the wallet and the planet,but lab experiments are now pointing to ways around their primary drawback: They can't berecharged over and over for decades.The need for grid-scale（电网规模的）battery storage is growing as increasing amounts of solar, wind, and other renewable energy come online.This year, America is committed to making the American electicity grid carbon-free by 2035.To even out dips in supply, much of that renewable power will have to be stored for hours or days, and then fed back into the grid.For Califonia alone,.it wants to deploy(部署）more than 8800 megawatts ofrechargeable battries by 2026,and ast week, the govemor of Califonia proposed $350 million in state funding to develop long-duration energy storage technologies.“"That trend will not go down.It will only continue to grow," says Mark Baggio, vice president for businessdevelopment at Zinc8 EnergySolutions, a zinc battery producer.“For power storage, Lithium-ion is the 800-pound gorilla," says Michael Burz, CEO of EnZinc, a zinc battery startup,"but lithium, a relatively raremetal that's only mined in a handful of countries, is too scarce and expensive to back up the worid's grids.We need an alternative to lithium.Zincbatteries may be one of the options."Non-rechargeable zinc batteries have been on the market for decades.More recently some zinc rechargeable batteries have also beencommercialized, but they tend to have limited energy storage capacity. Another technology, zinc flow cell batteries,is also making big steps. But it requires more complex pumps and tanks to operate.So,researchers are now working to improve other varieties including zinc-air cells.They say athough its urgent, there is a long way to go before they find a solution.【小题1】What do we know about grid-scale battery storage?A. It lacks financial support.B.It has crucial breakthroughs.C. It meets the public demands.D. Its market is huge.【小题2】What is Michae1Burz's attitude to zinc batteries for energy storage?A. Skeptical.B. Supportive.c. Conservative.D. Disappointed.【小题3】What does paragraph 4 mainty tell us about Zinc batteries?A. Their improvements.B. Their popularity.c. Their functions.D. Their disadvantages.【小题4】Which can be the best title for the text?A. Carbon free: a long-term goal to achieveB.Zinc batteries: a possible solution to power storageC. Renewable energy: the unlimited resource of powerD. Lithium-ion batteries: the front-runners for storing energy。

锂电池英文文献聚偏氟乙烯六氟丙烯基多孔固态锂电池电解质

Applied Surface Science 258 (2012) 4983–4989Contents lists available at SciVerse ScienceDirectApplied SurfaceSciencej o u r n a l h o m e p a g e :w w w.e l s e v i e r.c o m /l o c a t e /a p s u scMicroporous gel electrolytes based on amphiphilic poly(vinylidene ﬂuoride-co -hexaﬂuoropropylene)for lithium batteriesShicheng Yu a ,Lie Chen a ,b ,∗,Yiwang Chen a ,b ,∗,Yongfen Tong a ,caInstitute of Polymers,Nanchang University,999Xuefu Avenue,Nanchang 330031,ChinabJiangxi Provincial Key Laboratory of New Energy Chemistry,Nanchang University,999Xuefu Avenue,Nanchang 330031,China cSchool of Environmental and Chemical Engineering,Nanchang Hangkong University,696Fenghe South Avenue,Nanchang 330063,Chinaa r t i c l ei n f oArticle history:Received 20October 2011Received in revised form 26January 2012Accepted 26January 2012Available online 3 February 2012Keywords:PolyelectrolytesAtom transfer radical polymerization Ionic conductivitya b s t r a c tPoly(vinylidene ﬂuoride-co -hexaﬂuoropropylene)grafted poly(poly(ethylene glycol)methyl ether methacrylate)(PVDF-HFP-g -PPEGMA)is simply prepared by single-step synthesis directly via atom trans-fer radical polymerization (ATRP)of poly(ethylene glycol)methyl ether methacrylate (PEGMA)from poly(vinylidene ﬂuoride-co -hexaﬂuoropropylene)(PVDF-HFP).Thermal,mechanical,swelling and elec-trochemical properties,as well as microstructures of the prepared polymer electrolytes,are evaluated and the effects of the various contents and average molecular weights of PEGMA on those properties are also been investigated.By phase inversion technique,the copolymer membranes tend to form well-deﬁned microporous morphology with the increase of content and average molecular weight of PEGMA,due to the competition and cooperation between the hydrophilic PEGMA segments and hydrophobic PVDF-HFP.When these membranes are gelled with 1M LiCF 3SO 3in ethylene carbonate (EC)/propylene carbonate (PC)(1:1,v/v),their saturated electrolyte uptakes (up to 323.5%)and ion conductivities (up to 2.01×10−3S cm −1)are dramatically improved with respect to the pristine PVDF-HFP,ascribing to the strong afﬁnity of the hydrophilic PEGMA segments with the electrolytes.All the polymer electrolytes are electrochemically stable up to 4.7V versus Li/Li +,and show good mechanical properties.Coin cells based on the polymer electrolytes show stable charge–discharge cycles and deliver discharge capacities to LiFePO 4is up to 156mAh g −1.© 2012 Elsevier B.V. All rights reserved.1.IntroductionThe development of rechargeable lithium batteries has to be considered a milestone in the ﬁeld of energy storage and supply for mobile and/or portable electrical and electronic devices [1–4].However,solid polymer electrolytes (SPEs)proposed by Wright [5]using in lithium batteries remain too low for practical batteries operating at room temperature.In order to overcome the disad-vantage for practical usage,in the last two decades,so-called gel polymer electrolytes (GPEs)that are capable of holding stably a con-siderable amount of electrolyte solution within polymer matrices have attracted both basic research and industry attentions,as more promising materials for the practical use.GPEs are usually prepared with various matrix polymers such as polyacrylonitrile (PAN),[6]poly(methyl methacrylate)(PMMA),[7]poly(vinyl chloride)(PVC),[8]poly(vinyl pyrrolidone)(PVP),[9]poly(ethylene oxide)∗Corresponding authors at:Institute of Polymers,Nanchang University,999Xuefu Avenue,Nanchang 330031,China.Tel.:+8679183969562;fax:+8679183969561.E-mail addresses:chenlienc@ (L.Chen),ywchen@ (Y.Chen).(PEO)[10]and poly(vinylidene ﬂuoride)(PVDF)or poly(vinylidene ﬂuoride-co -hexaﬂuoropropylene)(PVDF-HFP)[11].Among them,PVDF-HFP is widely used because of its good mechanical and elec-trochemical stability with respect to nonaqueous electrolyte and electrode materials [12,13].When using GPEs,high ionic conductivity,good mechanical properties and excellent compatibility with the liquid electrolyte are considered as ideal characteristics for experimental usage.However a single polymer matrix could not meet all these charac-teristics simultaneously.Various modifying approaches have been developed to improve the performance of the PVDF-HFP-based electrolytes,such as choose different plasticizers to improve the absorption of electrolytes for the matrix [14–16],addition of var-ious inorganic additives to the electrolytes [17–22],and polymer blending to reducing the crystalline degree of plasticized polymer electrolytes.The main advantages of blend-based polymer elec-trolytes are simplicity of preparation and easy control of physical properties by changing the composition of blended polymer matri-ces [23],which have been known as efﬁcient means for modifying PVDF-HFP gel electrolytes at present [24].However,the poor com-patibility of the polymer matrices with the additions results in the large scale phase separation,and consequently limits the perfor-mance enhancement.0169-4332/$–see front matter © 2012 Elsevier B.V. All rights reserved.doi:10.1016/j.apsusc.2012.01.1464984S.Yu et al./Applied Surface Science258 (2012) 4983–4989Table1The ionic conductivities,percentage of swelling,tensile strength and elongation at break of the membranes with different feed weight ratios and average molecular weight of PEGMA.Sample The averagemolecular weightof PEGMA Feed weight ratio ofPVDF-HFP/PEGMAConductivity at25◦C(S cm−1)Swelling(%)Tensile strength atbreak(MPa)Elongationat break(%)PVDF-HFP10:00.92×10−3197.4 1.646.3 PVDF-g-PEG320(30%)3207:30.91×10−3175.8 1.440.3 PVDF-g-PEG320(50%)5:5 1.21×10−3210.1 1.846.6 PVDF-g-PEG320(70%)3:7 1.38×10−3243.7 2.032.5 PVDF-g-PEG475(30%)4757:30.79×10−3163.0 3.386.4 PVDF-g-PEG475(50%)5:5 1.66×10−3276.4 5.7100.2 PVDF-g-PEG475(70%)3:7 1.57×10−3246.6 6.278.7 PVDF-g-PEG950(30%)9507:3 1.13×10−3203.1 1.066.2 PVDF-g-PEG950(50%)5:5 1.96×10−3311.7 1.281.8 PVDF-g-PEG950(70%)3:7 2.01×10−3323.5 1.855.9Here,we report on a single-step simple synthesis of polymer electrolyte PVDF-HFP graft copolymer electrolyte membranes via atom transfer radical polymerization(ATRP)for lithium batteries. PVDF-HFP is directly grafted with hydrophilic poly(ethylene gly-col)methyl ether methacrylate(PEGMA)by ATRP fromﬂuorine atom on the main chain backbone.The hydrophilic PEGMA could improve the compatibility with PVDF-HFP by directly grafted to the polymer;on the other hand,the good afﬁnity of PEGMA with electrolytes also can provide the copolymer with good ionic con-ductivity by enhancing electrolyte uptakes.Thermal,mechanical, swelling and electrochemical properties,as well as microstructures of the prepared polymer electrolytes have been investigated sys-tematically,and the average molecular weights and contents of PEGMA in the copolymers have also been varied to understand the effects of these variables on the properties of the polymer elec-trolytes.2.Experimental2.1.MaterialsPoly(vinylideneﬂuoride-co-hexaﬂuoropropylene)(PVDF-HFP, M n=4×105g mol−1,Aldrich)was dehydrated in a vacuum oven at85◦C for24h.Copper(I)bromide(CuBr,Aldrich)was puri-ﬁed according to the cited literatures[25].Poly(ethylene glycol)methyl ether methacrylate(PEGMA,M n=300,475and 950g mol−1,Aldrich)and1,1,4,7,10,10-hexamethyl triethylene tetramine(HMTETA,Elf Atochem)were used as received.LiCF3SO3, ethylene carbonate(EC),propylene carbonate(PC),LiFePO4,and carbon black were Chemically Pure and purchased from Damao Chemicals,Tianjin,China.All the other organic solvents of AR grade were purchased commercially and used without further puriﬁca-tion.2.2.Preparation of PVDF-HFP-g-PPEGMA graft copolymerThe process for preparation of PVDF-HFP-g-PPEGMA is illus-trated in Scheme1.The PVDF-HFP and PEGMA with different feed weight ratios and different average molecular weights(shown in Table1)were dissolved in a certain amount of dried DMF at80◦C and30◦C respectively.These solutions were mixed together and the mixture was continuously stirred under nitrogen protection for30min,then,0.1ml HMTETA and0.028g CuBr were added.The mixture was heated to120◦C and stirred for24h.Finally,the mix-ture was washed by a large excess of methanol repeatedly,and dried under vacuum at60◦C for48h.2.3.Preparation of microporous membranes and polymer electrolytesPreparations of microporous membranes were used by phase inversion method.Appropriate amount of PVDF-HFP-g-PPEGMA was added into a mixture of acetone and deionized water(8:1w/w) and stirred continuously for24h.The obtained viscous solution was then casted onto a glass plate using a scalpel.The wet membrane was placed in a ventilating cabinet for12h to evaporate the ace-tone.Afterwards the membrane was dried to evaporate the residual impregnate at50◦C under vacuum for24h.This procedure gave a series of homogenous and mechanically strong membranes with various contents and average molecular weights of PEGMA.The membranes were then stored in a glove box (M Braun,Germany)under nitrogen atmosphere for further mea-surements.The thicknesses of the membranes were controlled to be in the range of150–200␮m.Polymer electrolytes were obtained by soaking blend membranes in liquid electrolytes consisting of1M LiCF3SO3in ethylene carbonate(EC)/propylene carbonate(PC)(1:1, v/v).The nomenclatures of the polymer electrolyte membranes with various average molecular weights and weight ratios are given in Table1.2.4.Coin cell assemblyCoin cells of2025conﬁguration were assembled using lithium metal as an anode,carboncoated lithium iron phosphate LiFePO4 as a cathode and copolymer membranes as separator electrolyte. The LiFePO4cathodes were prepared by a slurry coating process over the aluminums foil using doctor blade comprising of LiFePO4 (60%),carbon black(30%)and PVDF binder(10%).Coin cells were assembled inside an argonﬁlled glove box(M Braun,Germany)and subjected to electrochemical cycling studies.CH2CF CH2CF2CF2CFx y nCF3CH2CH3C C OFOCH2CF2CF2CFCF3m n+H3C CCH2COO CH2CH2O CH3hCuBr/HMTETAoCH2CH2O CH3p hScheme1.Synthesis route of PVDF-HFP-g-PPEGMA.S.Yu et al./Applied Surface Science258 (2012) 4983–49894985 2.5.Characterization methods2.5.1.FT-IR and1H NMR spectraThe Fourier transform infrared(FT-IR)spectra were measuredon a SHIMADZU IRPrestige-21FT-IR spectrophotometer.The pro-ton nuclear magnetic resonance(1H NMR)spectra were recordedon a Bruker ARX400MHz NMR spectrometer with d-DMSO as sol-vent and tetramethylsilane(ı=0)as internal reference.2.5.2.Surface analysisThe surface image of the membranes were investigated by scan-ning electron microscope(SEM),using an Environmental ScanningElectron Microscope(ESEM,FEI Quanta200).All the samples werecut into pieces,followed by the sputtering of a thin layer of gold.The morphologies of the membranes were then observed by theSEM with an accelerating voltage of30kV.2.5.3.Thermal and mechanical analysisThe thermal behaviors of the prepared samples were studied byusing thermal gravimetric analysis(TGA)and differential scanningcalorimeter(DSC).The TGA was performed using a Perkin-Elmerinstrument TGA7.Measurements were made by heating from roomtemperature to800◦C at a heating rate of20◦C min−1under anitrogen atmosphere.DSC measurements of the samples were car-ried out on a differential scanning calorimeter(Shimadzu DSC-60)under a nitrogenﬂow at a rate of20ml/min.The samples of about3mg were heated quickly to300◦C and held for5min to erase ther-mal history.Then,the samples were cooled to30◦C and reheated to300◦C at a rate of10◦C min−1.Tensile strength and elongation atbreak were measured with a CMT8502Machine model GD203A(Shenzhen Sans Testing Machine Co.,Ltd.,China)at a speed of5mm min−1.2.5.4.Electrochemical evaluationPolymer electrolytes were prepared by soaking a circular pieceof the membrane(diameter2cm)in the liquid electrolyte,the elec-trolyte uptakes(ı)were calculated using the relation:ı=W−W0W0×100%where W0is the mass of the dry membrane and W is the mass of the membrane after soaking with the electrolyte.The ionic conductivities of the polymer electrolytes were measured by the AC impedance method analyzer on a CHI660 electrochemical workstation(CH Instruments)coupled with a computer,over the temperature range from25to85◦C.The elec-trolyte sample was sandwiched between two SS electrodes and the impedance measurements were performed at amplitude of 10mV over the frequency range1Hz to100kHz.The cells were kept at each measuring temperature for a minimum of30min to ensure thermal equilibration of the sample at the temperature before measurement.From the thickness and surface area mea-surements,conductivities of the membranes were calculated from the following relationship:=d S×R bwhere ,d,S,and R b represent the ionic conductivity,the thick-ness,the resistance and the cross-sectional area of the membrane, respectively.The electrochemical stabilities were determined by linear sweep voltammetry(LSV)of Li/polymer electrolyte/SS cells,which is recorded in a three electrode cell(working electrode,reference electrode and counter electrode)at a scan rate of5.0mV s−1over the range of0–6V at room temperature.The electrochemical tests of the Li/polymer electrolyte/LiFePO4 cells were conducted in an automatic galvanostaticWavenumber (cm-1)Fig.1.The FT-IR spectrum of PVDF-HFP-g-PPEGMA copolymer. charge–discharge unit(neware),between2.5and4.0V at room temperature and a current density of20mA g−1.3.Results and discussion3.1.Synthesis of graft copolymersThe structure of the PVDF-HFP-g-PPEGMA graft copolymer was analyzed by FT-IR as shown in Fig.1.The copolymer was puri-ﬁed thoroughly before the tests of FT-IR and1H NMR spectra to rule out the interference of PEGMA homopolymer.FT-IR spectrum shows the appearances of three signiﬁcant absorbance bands at 2870,1730,and1100cm−1,ascribed to the stretching vibrations of the C H bond in the methylene,the ether C O C bond and car-bonyl O C O groups of PEGMA,respectively,which indicates the successfully grafting of PEGMA to PVDF-HFP via ATRP.The PVDF-HFP-g-PPEGMA graft copolymer was also conﬁrmed by1H NMR spectrum,and all resonance peaks have been assigned to appropriate protons as marked in Fig.2.The peaks of solvent(d-DMSO)and water appeared at2.5and3.3ppm,respectively.The head-to-head and head-to-tail of the protons resonance peaks of methylene in the PVDF-HFP units are respectively located at2.3and 2.9ppm.Grafting of PEGMA to the copolymer produces the peaks in the regions of1.2,1.3,3.2and3.5ppm associated to the proton signals of PEGMA segment,further supporting that the PEGMA was grafted by ATRP successfully.3.2.Membrane morphologyThe membranes with various compositions were prepared by the phase inversion method using acetone as the good solvent and deionized water as the non-solvent.During theﬁlm-casting process,mutual diffusion promptly occurs between solvent and non-solvent to make highly porous structure in polymer matrix. Fig.3shows SEM images of the morphologies of PVDF-HFP-g-PPEGMA microporous membranes with different compositions. From the SEM images,it can be seen that all the membranes develop well-deﬁned microporous morphologies.This suggests that two kinds of diffusion with opposite directions are competing in that the solvent component(acetone)is going to evaporate from the spread slurry while the non-solvent(water)is going to penetrate into it and then solidify the polymer,resulting in porous structure in the poly-mer matrix after evaporation of water.At the same time,the pore4986S.Yu et al./Applied Surface Science 258 (2012) 4983–4989Fig.2.The 1H NMR spectrum of PVDF-HFP-g -PPEGMA copolymer.distribution grows denser and more uniform with the increase of PEGMA from 30%to 70%.This could be attributed to the fact that the deionized water interacts with hydrophilic PEGMA segments through hydrogen bonds to induce better distribution of the water and pores.These results imply that the competition and cooper-ation between the hydrophilic PEGMA segments and hydrophobic PVDF-HFP induce the well-deﬁned microporous morphologies,and the pore size and porosity could be readily controlled by control-ling the content or the molecular weight of hydrophilic PEGMA segments.3.3.Thermal propertiesFig.4illustrates the DSC curves of the PVDF-HFP-g -PPEGMA graft copolymers,along with the parent PVDF-HFP for compari-son.The melting temperature of pure PVDF-HFP is 140◦C,while the polymer electrolyte membranes have slightly lower melting points in a close range of 122–137◦C.In the graft copolymer,both PEGMA and VDF units are miscible with each other and their interactions destroy the molecular stacking arrangement.There-fore,the decreased melting points of the electrolytes membranes result from the reduction in crystallinity of the electrolyte mem-branes.The melting temperatures of graft copolymers are related to the content of graft chain.The different molecular weights of macromonomers have different polymerization activity.The differ-ent tendency of melting temperatures varying with feeding ratio of PEGMA is probably due to the nonhomogeneous graft of the PEGMA to PVDF-HFP.The macromonomer PEG950has a little change in graft content while different feeding ratio is given in the graft polymerization.Therefore,the melting temperatures of PVDF-g -PEG950are almost same even different contents of PEG.Thermal stability is also vital to guarantee acceptable perfor-mance at elevated temperatures.The thermal stabilities of the PVDF-HFP-g -PPEGMA microporous membranes were analyzed by TGA and the corresponding results are shown in Fig.5.The mem-branes are thermally stable with no obvious weight loss observed less than 225◦C for all samples.Although the decomposition tem-peratures decrease with respect to PVDF-HFP with a value of 450◦Cdue to the less thermal stable PEGMA segments,they are suitable as polymer electrolytes for lithium batteries.A little weight loss at about 100◦C is ascribed to a small amount of water remained in the samples.3.4.Mechanical propertiesTable 1shows the mechanical properties of the PVDF-HFP-g -PPEGMA microporous membranes and the pristine PVDF-HFP membrane in dried condition.As seen in Table 1,most of the micro-porous membranes with grafted PEGMA show higher values of elongation at break in comparison with pristine PVDF-HFP mem-brane,suggesting that the addition of PEGMA,a soft segment,helps in the elongation of the graft copolymer membranes.Similarly,the tensile strength of the modiﬁed copolymers is also improved by incorporating PEGMA moiety.Moreover,mechanical properties of the microporous membranes depend on the composition ratio and the average molecular weight of PEGMA.The copolymer mem-branes containing PEGMA with the average molecular weight of 475exhibit the best mechanical properties,especially for PVDF-g -PEG 475(50%)with tensile strength of 5.7MPa,and elongation at break of 100.2%.The whole enhanced mechanical properties are beneﬁcial in the fabrication of polymer lithium ion batteries.3.5.The electrolyte uptakes of the polymer electrolytes membranesElectrolyte uptake is a serious inﬂuent factor in polymer lithium ion batteries,and the electrolyte within the membrane provides a carrier for the Li +and maintains high ionic conductivity.The liquid electrolyte uptakes of the polymer membranes are shown in Fig.6and Table 1.The saturated electrolyte uptake increases with the average molecular weight and content of PEGMA increas-ing,and reaches a maximum of 323.5%in PVDF-g -PEG 950(70%),which is 1.5times higher than in PVDF-HFP.In the microporous membranes,liquid electrolyte is not only trapped in the pores but also swelled into the matrix.Due to the higher afﬁnity with the electrolyte solution than PVDF-HFP,the PEGMA tends to suck andS.Yu et al./Applied Surface Science258 (2012) 4983–49894987Fig.3.The SEM images of PVDF-HFP-g-PPEGMA microporous membranes:(a)PVDF-g-PEG320(70%);(b)PVDF-g-PEG320(50%);(c)PVDF-g-PEG320(30%);(d)PVDF-g-PEG475 (70%);(e)PVDF-g-PEG475(50%);(f)PVDF-g-PEG475(30%);(g)PVDF-g-PEG950(70%);(h)PVDF-g-PEG950(50%);(i)PVDF-g-PEG950(30%)as shown in Table1.100110120130140150160Temperature (o C)Fig.4.Differential scanning calorimetric(DSC)scans of pristine PVDF-HFP mem-brane and PVDF-HFP-g-PPEGMA copolymer membranes,which prepared with different average molecular weight and weight ratios as shown in Table1.100200300400500600700Temperature (ºC)Fig.5.TGA thermograms of PVDF-HFP-g-PPEGMA graft copolymer membranes with different feed weight ratios and average molecular weight of PEGMA as shown in Table1.4988S.Yu et al./Applied Surface Science258 (2012) 4983–4989100200300400PVDF-g-PEG 950PVDF-g-PEG 47530%30%30%70%70%50%50%50%PVDF-g-PEG 320E l e c t r o l y t e u p t a k e (w t . %)PVDF-HFP Fig.6.The liquid electrolyte uptakes of the polymer membranes.storage more liquid electrolytes.On the other hand,well-deﬁned morphology with good pore size and pore distribution induced by the amphiphilic membranes dramatically enhances the electrolyte uptakes.3.6.The ionic conductivities of polymer electrolytes membranesFig.7shows the temperature dependence of the ionic conduc-tivities of the membranes in the form of Arrhenius plots.There are three ways for Lithium ions to transfer within the porous poly-mer electrolyte:through liquid electrolyte stored in the pores,amorphous domains swelled by liquid electrolyte and along the polymer chains.The transfer along polymer chains is much slower than transfer through pores and amorphous domains.Delightfully,conductivity increased linearly with increasing of temperatures in the polymer electrolytes,indicating that ion transport is decou-pled from the polymer segmental movement and mainly relays on liquid electrolyte in pores and amorphous domains.The ionic conductivities of all the present polymer electrolyte systems over the whole temperature range investigated (25–85◦C)are higher than 10−3S cm −1which is the typical ion conductivity of com-mercially available electrolyte.The conductivity increases with the2.7 2.8 2.93.0 3.1 3.2 3.3 3.4-3.2-3.0-2.8-2.6-2.4-2.2-2.0-1.8l o g s (S c m -1)1000/T (K -1)Fig.7.Temperature dependence of the ionic conductivity for PVDF-HFP-g -PPEGMApolymer electrolytes membranes with different feed weight ratios and average molecular weight of PEGMA as shown in Table 1.325460.00000.00250.00500.00750.01000.0125C u r r e n t ( A )Voltage ( V )PVDF-HFPPVDF-g-PEG 950(70%) PVDF-g-PEG 950(50%) PVDF-g-PEG 950(30%)Fig.8.Linear sweep voltammetry curves of the cells prepared with gel polymer electrolytes containing different content of PEGMA (average molecular weight 950).average molecular weight and content of PEGMA increasing,and the PVDF-g -PEG 950(70%)shows the highest conductivity,which reaches 2.0×10−3S cm −1at 25◦C and the value on the order of 10−2S cm −1at 85◦C,respectively.This trend agrees well with the change of liquid electrolyte uptakes.This is attributed to the high liquid electrolyte uptakes provided by the high content of PEGMA facilitating the ion transportation.What is more,the ether bonds in the PEGMA segments could form complexities of O and Li +,further driving the Li +to migration and transfer.Arrhenius plot for estimation of the activation energy (E a ),the minimum energy required for Li +transportation across the mem-brane.The activation energy for Li +transport,E a ,can be obtained by using the Vogel–Tamman–Fulcher relation= 0T −1/2exp−E aT −T owhere is ionic conductivity, 0is pre-exponential factor and T 0is glass transition temperature.The E a values decreased from 11.37to 8.51kJ mol −1with the PEGMA content and the aver-age molecular weigh increasing in the membrane matrix.For membranes,and the value of PVDF-g -PEG 950(70%)reach the min-imum of 8.51kJ mol −1.The low activation energy reveals positive temperature-conductivity dependencies for Li +transportation.3.7.Electrochemical propertiesLinear sweep voltammetry curves of the cells prepared with gel polymer electrolytes of the selected membranes with good ionic conductivities,where the average molecular weigh of PEGMA-containing is 950,are presented in Fig.8,and that of unmodiﬁed polymer also be presented for comparison.A rapid rise in current is observed around 4.7V (vs.Li/Li +)and continued to increase as the potential is swept,which is associated with the oxidative decom-position of the gel polymer electrolyte.The values are beyond the electrochemical reference of 4.4V,meaning that the gel polymer electrolytes have a suitable electrochemical stability for the appli-cation in lithium ion batteries.The polymer electrolytes with different content of PEGMA (average molecular weight 950)have also been evaluated for charge/discharge performance in Li/LiFePO 4cells at room tem-perature.The ﬁrst cycle charge–discharge properties at a current density corresponding to 0.1C-rate are compared in Fig.9.Also,content of PEGMA exerts inﬂuence on the charge/discharge perfor-mance.The cell based on the polymer electrolyte of PVDF-g -PEG 950(50%)delivers charge and discharge capacities of 156mAh g −1.The performances of the cells with polymer electrolyte membraneS.Yu et al./Applied Surface Science 258 (2012) 4983–498949892004060801001201401602.83.03.23.43.63.8V o l t a g e ( V )Specific capacity ( mAhg -1)PVDF-g-PEG 950(70%) PVDF-g-PEG 950(50%) PVDF-g-PEG 950(30%)Fig.9.Initial charge–discharge properties of the cells prepared with gel polymer electrolytes containing different content of PEGMA (average molecular weight is 950).4080120160200D i s c h a r g e c a p a c i t y (m A h g -1)Cycle numberFig.10.Cycle performance of Li/PGE/LiFePO 4cells with polymer electrolyte of PVDF-g -PEG 950(50%).PVDF-g -PEG 950(70%)and PVDF-g -PEG 950(30%)are slightly lower and the discharge capacities of 152and 130mAh g −1are obtained,respectively.Fig.10shows the repeated charge–discharge capacities at 0.1C on cycling of Li/LiFePO 4cell with polymer electrolyte membrane PVDF-g -PEG 950(50%).After 30th cycle,the discharge capacity of 151mAh g −1was achieved.The result shows that the discharge capacity is well retained for the membrane even after 30cycles.The result,in turn,indicates that the electrolyte has good compatibility with both the electrodes,especially lithium metal.4.ConclusionsA single-step synthesis of PVDF-HFP graft copolymer with PEGMA electrolyte membranes via ATRP has been demonstrated.PEGMA segment directly grafted onto PVDF-HFP efﬁciently avoids the phase separation and produces the copolymers membranes with uniform and good porosity by phase inversion method.Due to the strong afﬁnity of the hydrophilic PEGMA segments with the electrolytes,the electrolyte uptakes and ion conductivities are dra-matically improved with respect to the pristine PVDF-HFP,and the average molecular weight and content of PEGMA exert great on the properties.The highest electrolyte uptake and ion conductivity at room temperature is 323.5%and 2.01×10−3S cm −1respectively.All the membranes have no signiﬁcant weight loss up to 225◦C,and the gel electrolytes are electrochemically stable up to 4.7V versus Li/Li +.In addition,the discharge capacities are well retained for the membranes even after 30cycles.The results reveal that this type of microporous gel electrolytes based on PVDF-HFP-g -PPEGMA is very promising for improving the properties and qualiﬁes as a potential application in lithium battery.AcknowledgementFinancial support for this work was provided by the National Natural Science Foundation of China (21164007).References[1]J.R.MacCallum,C.A.Vincent (Eds.),Polymer Electrolyte Review,vols.1and 2,Elsevier Applied Science,London,1987–1989.[2]J.S.Tonge,D.F.Shriver,in:i (Ed.),Polymers for Electronic Applications,CRC Press Inc.,Boca Raton,FL,1989(Chapter 5).[3]F.M.Gray,Polymer Electrolytes,The Royal Society of Chemistry,Cambridge,1997.[4]W.A.Van Schalkwijk,B.Scrosati (Eds.),Advances in Lithium-Ion Batteries,Kluwer Academic/Plenum Publishers,New York,2003.[5]P.V.Wright,Br.Polym.7(1975)319–327.[6]F.Croce,F.Gerace,G.Dautzenberg,S.Passerini,G.B.Appetecchi,B.Scrosati,Electrochim.Acta 39(1994)2187–2194.[7]O.Bohnke,G.Frand,M.Rezrazi,C.Rousselot,C.Truche,Solid State Ionics 66(1993)97–104.[8]G.Pistoia,A.Antonini,G.Wang,J.Power Sources 58(1996)139–144.[9]S.Passerini,J.M.Rosolen,B.Scrosati,J.Power Sources 45(1993)333–341.[10]J.Y.Song,Y.Y.Wang,C.C.Wan,J.Power Sources 77(1999)183–197.[11]K.Tsunemi,H.Ohno,E.Tsuchida,Electrochim.Acta 28(1983)591–595.[12]A.Magistris,E.Quartarone,P.Mustarelli,Y.Saito,H.Kataoka,Solid State Ionics152–153(2002)347–354.[13]N.Chung,D.Kim,J.Power Sources 124(2003)148–154.[14]P.Raghavan,X.Zhao,J.-K.Kim,J.Manuel,G.S.Chauhan,J.-H.Ahn,C.Nah,Electrochim.Acta 54(2008)228–234.[15]Z.Ren,Y.Liu,K.Sun,X.Zhou,N.Zhang,Electrochim.Acta 54(2009)1888–1892.[16]V.Gentili,S.Panero,P.Reale,B.Scrosati,Ionics 13(2007)111–116.[17]R.Mogi,M.Inba,S.Jeong,Y.Iriyama,T.Abe,Z.Ogumi,J.Electrochem.Soc.149(2002)A1578–A1583.[18]H.Ota,K.Shima,M.Ue,J.Yamaki,Electrochim.Acta 49(2004)565–572.[19]D.Aurbach,Y.Talyosef,B.Markovsky,E.Markevich,E.Zinigrad,L.Asraf,J.S.Gnanaraj,H.J.Kim,Electrochim.Acta 50(2004)247–254.[20]M.Ishikawa,H.Kawasaki,N.Yoshimoto,M.Morita,J.Power Sources 146(2005)199–203.[21]K.Abe,higoe,H.Yoshitake,M.Yoshio,J.Power Sources 153(2006)328–335.[22]J.A.Choi,S.M.Eo,D.R.MacFarlane,M.Forsyth,E.Cha,D.W.Kim,J.Power Sources178(2008)832–836.[23]D.Saikia,H.Y.Wu,Y.C.Pan,C.P.Lin,K.P.Huang,K.N.Chen,G.T.K.Fey,H.M.Kao,J.Power Sources 196(2011)2826–2834.[24]R.Zhong,K.N.Sun,Y.Y.Liu,X.L.Zhou,N.Q.Zhang,X.D.Zhu,Solid State Ionics180(2009)693–697.[25]L.Bao,Y.W.Chen,W.H.Zhou,Y.Wu,Y.L.Huang,J.Appl.Polym.Sci.122(2011)2456–2466.。

文献报告-An ultrafast rechargeable aluminium-ion battery

1Department
of Chemistry, Stanford University Nature
文章中设计的新型铝电池：
1)结构：
① 负极——铝箔（厚度15-250nm） ② 正极——泡沫石墨 ③ 电解质溶液——有机盐[EMIm]Cl 与氯化铝的混合物
2)性能：
① 稳定放电电压——约2V
② 比容量——70mA/g
③ 库仑效率——98%
④ 电流密度——4000mA/g
⑤ 循环稳定性——7500次（目前最
高1000次左右） ⑥ 商业优势——低成本、安全性高
电极材料及电解质测试
(002)
原始石墨、热解石墨和泡沫
石墨的XRD检测结果
XRD衍射峰相同，结构相同布拉格方程λ=2dsinθ 面间距d=3.35A’
a) 不同比值的AlCl3/[EMIm]Cl电解液的恒电流充放电曲线 b) AlCl3/[EMIm]Cl为1.3电解液的拉曼光谱
铝离子电池研究
常见二次电池介绍
常见金属阳极材料性能对比
锂离子电池介绍
• (1) 工作电压高：工作电压3.6V，是镍镉或镍氢电池的3倍
• (2) 比能量高：目前比能量已达到150-220 Wh/Kg，是镍镉电池的3
倍，镍氢电池的1.5倍
• (3) 循环寿命长：循环寿命已达1000次以上
• (4) 自放电小：月自放电率仅为6-8%，远低于镍镉或镍氢电池
Al/PG(热解石墨)电池的充放电曲线和循环稳定性
电池工作原理探究
c)Al/泡沫石墨电池的充放电循环稳定性及库仑效率 d) Al/泡沫石墨电池在不同充放电电流密度下的稳定性及库仑效率
总结与思考：
本文创新点：
1)正极采用泡沫石墨，实现电池快速充电，充电电流密度达到5000mA/g，在1分钟内可完成充电。 2)电池的充放电循环稳定性极高，循环达到7500次保持稳定的比容量。

3 Lithium-Ion Batteries (国外专著)

C hapter 3C arbon Anode MaterialsZ empachi O gumi and H ongyu W angAccompanying the impressive progress of human society, energy storage technologies become evermore urgent. Among the broad categories of energy sources, batteries or cells are the devices that successfully convert chemical energy into electrical energy. Lithium-based batteries stand out in the big family of batteries mainly because of their high-energy density, which comes from the fact that lithium is the most electropositive as well as the lightest metal. However, lithium dendrite growth after repeated charge-discharge cycles easily will lead to short-circuit of the cells and an explosion hazard. Substituting lithium metal for alloys with aluminum, sili-con, zinc, and so forth could solve the dendrite growth problem. 1 Nevertheless, thelithium storage capacity of alloys drops down quickly after merely several charge-discharge cycles because the big volume change causes great stress in alloy crystal lattice, and thus gives rise to cracking and crumbling of the alloy particles. Alternatively, Sony Corporation succeeded in discovering the highly reversible, low-voltage anode, carbonaceous material and commercialized the C/LiCoO 2rocking chair cells in the early 1990s. 2 Figure 3.1 schematically shows the charge-discharge process for reversible lithium storage in carbon. By the application of a lithiated carbon in place of a lithium metal electrode, any lithium metal plating process and the conditions for the growth of irregular dendritic lithium could be considerably eliminated, which shows promise for reducing the chances of shorting and over-heating of the batteries. This kind of lithium-ion battery, which possessed a working voltage as high as 3.6 V and gravimetric energy densities between 120 and 150 Wh/kg, rapidly found applications in high-performance portable electronic devices. Thus the research on reversible lithium storage in carbonaceous materials became very popular in the battery community worldwide.I n fact, the ability of layer-structured carbon to insert various species was well known by the latter half of the 1800s. The ability of graphite to intercalate anionspromoted exploration into the use of a graphite cathode for rechargeable batteries. 3Juza and Wehle described carbon lithiation studies in the middle of last century. 4M. Yoshio et al. (eds.), Lithium-lon Batteries , 49DOI 10.1007/978-0-387-34445-4_3 © Springer Science + Business Media LLC 2009Z. Ogumi and H. Wang (*)D epartment of Energy and Hydrocarbon Chemistry ,G raduate School of Engineering, Kyoto University , Kyoto 606-8501 , Japanw anghongyu@50 Z. Ogumi and H. Wang Guerard and Herold completed pioneering research of lithium intercalation into graphite and other less-ordered carbons such as cokes by a vapor transport method in 1975. 5In 1976, Besenhard et al. 6,7tried intercalating Li +into graphite electro-chemically in the electrolytes of lithium salts dissolved in solvents of DME and DMSO, but obtained Li +-solvent-graphite ternary intercalation compounds because of the strong affinities between Li +and the solvent molecules. In 1980, Basu uti-lized lithium-graphite intercalation compounds (GIC) in lithium-based secondary batteries for the first time when he used LiCl-KCl melting salts as the electrolytes for high-temperature-type batteries. 8As for the ambient temperature-type batteries, Ikeda and Basu applied patents on Li-GIC as anode materials in 1981 and 1982, respectively. 9,10In 1983, Yazami and Ph. Touzain succeeded in synthesizing Li-GIC electrochemically using a solid organic electrolyte. 11The ease with which lithium can be intercalated and deintercalated from carbon has led to numerous studies on lithiated carbon anodes for battery application.3.1 Staging Phenomenon of Li-GICG raphite intercalation compounds have one significant feature: the staging phe-nomenon, which is characterized by a periodic sequence of intercalant layers (say, lithium cations) between graphite layers. The nth-stage compound consists of inter-calant layers arranged between every n graphite layers. The first-stage lithiumgraphite intercalation compound has the stoichiometry of LiC6with the specificcapacity of 372 mAh/g (850 mAh/cm 3), a theoretical saturated value of lithiumstorage for graphite under normal pressure. The staging phenomenon can be easily F ig. 3.1M odel for lithium-ion batteries3 Carbon Anode Materials 51 monitored and controlled by the electrochemical reactions of carbons in Li +-containing electrolytes, for instance, galvanostatic (constant current) charge-dis-charge 12,13and slow cyclic voltammetry 14–17(CV) have proven to be particularly useful electrochemical methods. In the case of galvanostatic charge-discharge of graphite electrodes in Li +-containing electrolytes, the reversible plateaus on the potential curves indicate two-phase regions in the lithium-graphite phase diagram, whereas reversible current peaks demonstrates the two-phase regions in the CV. In conjunction with the electrochemical techniques, some physical methods have been applied to shed light on the stage occurrence and transitions during lithium interca-lation into and deintercalation from graphite host. These methods include in situ 12,18 and ex situ 19XRD, in situ laser raman spectra, 20STM, 21and so forth. Different schemes for stage transitions have been proposed. Main discrepancies lay in the ascriptions of higher stages. Actually, more or less turbostratic disorder (randomly stacking of graphene layers) is present in most synthetic graphite samples. Dahn’s group found that turbostrtic disorder frustrates the formation of staged phases of Li-GIC, especially for higher stages. 22,233.2 Solid Electrolyte Interface Film FormationA nother important feature for lithium graphite intercalation compounds in Li +-containing electrolytes is the formation of s o lid e l ectrolyte i n terface (SEI) film. During the first-cycle discharge of a lithium/carbon cell, a part of lithium atoms transferred to the carbon electrode electrochemically will react with the nonaque-ous solvent, which contributes to the initial irreversible capacity. The reaction products form a Li +-conducting and electronically insulating layer on the carbon surface. Peled 24named this film as SEI. Once SEI formed, reversible Li +intercala-tion into carbon, through SEI film, may take place even if the carbon electrode potential is always lower than the electrolyte decomposition potential, whereas further electrolyte decomposition on the carbon electrode will be prevented.B esenhard et al. 25proposed the SEI formation mechanism of graphite via inter-calation of solvated Li +as schematically illustrated in Fig. 3.2 . Ogumi’s group later verified this assumption in their systematic studies. 26–28It is generally accepted that SEI film plays a very important role in the electrochemical performance of carbon anodes, especially for graphitic carbons, which are much more sensitive to the electrolyte composition. Ethylene carbonate (EC) and propylene carbonate (PC) are the most widely used high-permittivity solvents for Li +-ion batteries. PC-based electrolytes demonstrate superior low-temperature performance to EC-based elec-trolytes mainly because of their different melting points (mpPC −49°C, mpEC39°C).However, it is well known that EC-based electrolytes are suitable for graphite, whereas PC-based electrolytes are not compatible with graphite anodes, since PC decomposes drastically on graphite surface and exfoliates graphite particles. 29–32 Thus how to successfully apply graphite in PC-based electrolytes becomes a big challenge in the Li +-ion battery community.52 Z. Ogumi and H. WangIn fact, EC is very similar to PC in chemical structure, but only differs by one methyl group. Why the introduction of this single methyl into cyclic carbonate causes graphite exfoliation and electrolyte decomposition aroused the steric effecton solvent cointercalation. Chung et al. 33, 34 added in the second methyl group intocarbonate structure and got two geometric isomers, cis- and trans- butylene carbon-ates (BC). In the trans-BC based electrolytes the decomposition of the electrolyte and exfoliation were mild, but very drastic in cis-BC based one. This experimentin turn verified the significance of SEI formation mechanism via Li +-solventco-intercalation. Nakamura et al. 35 studied the performance of graphitic carbon inthe non-aqueous electrolytes containing the binary solvent mixtures of PC/DEC, PC/DMC and PC/EMC. They found that once the PC concentration decreased toless than [PC]:[Li +]£ 2, the PC decomposition becomes considerably suppressed.Xu et al. 36recently showed that the salt of lithium bis(oxalato) (LiBOB) can stabilize F ig. 3.2 S EI formation mechanism of graphite via intercalation of solvated Li + . Reprinted from, 25copyright (1995), with permission from Elsevier Ltd.3 Carbon Anode Materials 53graphitic carbon in neat PC and support reversible Li + intercalation. Most recently,Jeong et al. 37 succeeded in reversibly intercalate Li + into the electrolyte of 2.72 MLiN(SO 2C 2F 5)2 dissolved in 100% PC and suggested that ion-solvent interactions would be a vital factor for SEI formation in PC-based electrolytes. On the other hand, many studies have been devoted to designing effective SEI formation inPC-based electrolytes by some additives, such as vinylene cyclic carbonate,38crown ether, 39, 40 fluoroethylene carbonat, 41 ethylene sulfite, 42 catechol carbonate, 43, 44vinyl acetate, 45 and so forth. In some cases, the additives will decompose at potentials higher than PC decomposition potential on graphite anode. That means, prior to PC decomposition and graphite exfoliation, the decomposition products of these addi-tives like ethylene sulfite could form a robust SEI film covering graphite anode surface to protect it from direct contact with PC-based electrolytes. In other cases, some solvents like crown ether, DMSO, and tetraglme have much stronger affinitywith Li + than PC. 46C ombined with their extensive studies on the passivation films on lithium metal in nonaqueous electrolytes, 47– 49 Aurbach’s group carried out a series of work on theelectrochemical behavior of graphite in Li +-ion batteries. 50– 54 The importance of SEIstructure and chemical composition for graphite performance was highlighted. For instance, ROCO 2 L i and (CH 2O CO 2L i) 2 besides Li 2C O 3 were identified as the key components for the construction of effective SEI passivating graphite electrodes at ambient temperature. These conclusions were verified further by other groupsusing electron energy loss spectroscopy (EELS), 55 auger electron spectroscopy)(AES), temperature programmed decomposition mass spectroscopy (TPD-MASS), 56 and so forth.A s the performance of Li +-ion batteries at elevated temperatures (50–70°C) is relevant to their safe utilizations, studies on SEI film properties at elevated tempera-tures have been pursued recently. 57– 62 It was found that metastable species likeROCO 2 L i within the SEI layer will decompose into more stable products such as LiC 2O 3 and LiF at elevated temperatures. This leaves more pores in SEI layer and exposes the graphite-lithium surface to electrolytes, causing more irreversible capacities during continuous cycling. Actually, some companies have used the“aging” process to construct stable SEI film on electrodes for Li +-ion batteries,which is based on the above phenomenon. After fabrication, the Li +-ion batterieswere charged and stored at elevated temperature for certain times before sale in markets. Thus the SEI film is composed mainly of stable species like LiC 2O 3and LiF and prove to be robust and effective for passivating the carbon electrodes.3.3 C orrelations of Carbon’s Structuresand Electrochemical PerformanceCarbonaceous materials have found wide applications in electrochemical technolo-gies. This fact, in part, may be attributed to their advantages like good thermal and electrical conductivities, low density, adequate corrosion resistance, low thermal54 Z. Ogumi and H. Wang expansion, low elasticity, low cost, and high purity; however, to a larger extent, it is due to their flexibility and complexity in functional structures. There are different kinds of structure and each has a profound effect on the electrochemical perform-ance of carbon.T he smallest dimensional structure is the bonding form between C atoms. Carbon atoms bind themselves by sp 3,sp 2, and sp hybrid orbitals. Carbonaceous materials are generally made up from repeating sp 2-bonding C–C atoms, which construct the planar hexagonal networks (honeycombs) of C atoms called graphene layers. There are some cases of doping foreign elements like P, B, N, Si into graph-ene layer to disturb the sp 2-bonding C–C order and change the lithiation behavior of carbon. For instance, Dahn’s group has tried doping B 63or N 64into C–C net-works and found that N embedded into C lattice shifts the reversible capacity to lower voltage, whereas the substitution of B for C could increase the working volt-age. As a result, N decreases the reversible capacity but B enlarges the reversible capacity for Li +storage. Besides the bulk of carbon, at the edge of graphene layers or some defects, there are some sp 3bondings of C–C (dangling carbon) or C–H, C–OH, C–COOH, and so forth; sp 3bonding C seems more chemically active than sp 2C–C in the bulk of carbon. Some groups have found the evidence for sewing the adjacent graphene layers’ edges into close-edge surface structure for graphitic car-bon, very similar to carbon nanotube. 65The coupling process of adjacent graphene layers’ edges is through the joint of the dangling carbon atoms. The close-edge graphitic carbon delivers very small initial irreversible capacity since the chemi-cally stable surface suppresses the SEI formation.A ctually, each graphene layer can be considered to be a superconjugated macro-molecule. Van der Waals force stacks these sheets into ordered structures called crystallites. There are two patterns for orderly stacking graphene layers into ideal graphite crystallites, one with the sequence of …ABAB… and the other with the sequence of …ABCABC…., as shown in Fig. 3.3 . The former possess a little more thermally stable hexagonal symmetry, while the latter has a rhombohedral sym-metry. Graphite usually comprises both crystal structures, but the rhombohedral content seems always less than 30%. 66–68Several studies have suggested that a high rhombohedral content could suppress the exfoliation effects during the cointercala-tion of solvated Li +into graphene layers, especially for PC-based electrolytes. After a careful investigation on the effects of high-temperature annealing and post-burn-off treatment of synthetic graphite samples, Spahr et al. 69recently concluded that the presence of rhombohedral stacking pattern in the bulk of graphite crystallite has almost no direct influence on the initial irreversible capacity. The irreversible capacity associated with PC-based electrolytes decomposition and graphite exfolia-tion appears to be graphite surface-dependent.T he Van der Waals force between graphene layers is so weak that the planes easily slide. Consequently, varying degrees of stacking faults are caused by random rotations and translations of graphene sheets within the carbon matrix. Most carbon atoms deviate from the regular position and the periodic stacking no longer main-tains. This type of structure is called turbostratic structure. Its X-ray diffraction (XRD) pattern only shows broad (00l) and asymmetric (hk) diffraction peaks 703 Carbon Anode Materials 55F ig. 3.3C rystal structures of graphite, hexagonal ( u pper) and rombohedral ( b elow)because the three-dimensional regularity is poor but the roughly parallel and ran-dom stacking of graphene layers remain detectable. For turbostratic carbon, inter-layer distances are somewhat diffused and on average larger than that of graphite. Disordered carbons fall into two types: soft carbon, whose turbostratic disorder is easily removed by heating to high temperature (near 3,000°C), and hard carbon, for which it is difficult to remove the turbostratic disorder at any temperatures. Franklin has proposed a model for the structures of soft and hard carbons as shown in Fig. 3.4 .T here are many studies on the relationship between turbostratic structure and carbon lithiation behavior. In the comprehensive work of Dahn’s group, 71,72an auto-mated structure-refined program has been developed for XRD data collected on disordered carbons. Based on this program to calculate some fundamental param-eters, they tried to quantify the Li +storage capacity of carbon. This program has been used for more than 40 soft carbons and proved to be valuable. On the other56 Z. Ogumi and H. Wang hand, Osaka Gas research group derived the following equation from the view pointof mathematics to predict the attainable capacity of carbon 73:()1/222002c c c a c c a c c 372/[1/] 12(3)/.Q d L d L d L d −−−⎡⎤=++++⎣⎦(3.1) T oshiba research group discovered the relationship (as shown in Fig. 3.5 ) between carbon’s discharge capacity and the average layer distance ( d 002 ) from their experi-mental data for several series of soft carbons. 74 This figure actually reflects twotrends for the choice of carbonaceous materials in Li + -ion batteries. The d 002value of 0.344 nm in fact corresponds to turbostratic disordered carbon. We can take theminimum at 0.344 nm as the starting point and guide our attentions into two directions: one is toward d 002 value smaller, which means obtaining more graphitic carbon; the other way is toward d 002 value bigger, which implies the selection of more disordered carbon. Both ways can obtain carbon with high capacity.T atsumi et al. found the relationship between P 1 and the capacity in the potential range from 0 to 0.25 V vs. Li/Li + for soft carbons. 75 The P 1 stands for the volume ratio of ordered-stacking graphitic crystallites in carbon. In contrast, Dahn et al. used P parameter to indicate the probability of random stacking between the adjacenttwo graphene layers. 22, 71, 72, 76 It appears that P 1 = 1 − P . Moreover, Tstsumi et al. correlated the capacity delivered in the potential range from 0.25 to 1.3 V vs. Li/Li +with 1 − P 1 , which is the fraction ratio of turbostratic structure. The relationships between P 1 , 1 − P 1 with the reversible capacities at different potential ranges is shown in Fig. 3.6 .Fujimoto et al. calculated the projected probability function and Fig. 3.4 S tructure models for soft ( u pper ) and hard ( b elow )carbons3 Carbon Anode Materials 57measured (hk) XRD peaks of some soft carbons to simulate turbostratic structurein two adjacent parallel graphene layers. 77– 80 The calculated pattern of twisted lay-ers demonstrates a “moiré”-like structure with different stacking orders rangingfrom AB to AA. Li + can intercalate into AA stacking “islands,” but cannot enter F ig. 3.6 T he relationships between P 1 and 1- P 1 with the reversible capacities ( x in Li x C 6 ) at dif-ferent potential ranges for soft carbon. Reproduced with permission from, 75 copyright (1995), The Electrochemical Society58 Z. Ogumi and H. Wang into the AB stacking portion. The maximum Li +storage capacity for turbostraticstructure can be estimated as Li0.2C6by extrapolation in Tatsumi’s study.T he surface structure of carbon is also important for battery performance. There are two types of surfaces for carbon as shown: one is the basal plane of graphene layers, and the other is the edge plane located at the border of each graphene layers. The studies on Li +intercalation into highly oriented pyrolytic graphite (HOPG) showed that the basal plane is inert, whereas the edge plane is active for Li +inser-tion. 81,82Li +intercalated into graphite bulk mainly through the edge planes, and only a small part of Li +can pass through the defects of basal planes into graphite bulk. In addition, there are different kinds of functional groups on the edge planes, which can affect the Li +intercalation greatly. Some papers also reported the direct relationship between specific surface area and the irreversible capacity.A nother structure for carbons is texture, the ways that the crystallites joined together. Texture is often characterized by the degree of orientation from random to systematic arrangement. If the crystallite size is small enough and there is no spe-cific orientation, the carbon appears to be amorphous. Texture control cannot change the properties of individual crystallites but can alter the properties of the agglomerates of these crystallites like electricity and active surface area. The com-parative study 83of mesophase-pitch-based carbon fibers with different textures showed that the radical texture is more favorable for Li +intercalation than the con-centric texture, but the radical texture is more easily broken into pieces by solvent cointercalated Li +.A ggregations of different types of textures can be considered to be a special structure of carbon in a bigger scale. Because electrochemical properties depend partially on the macroscopic structure of the electrode material, the state of aggre-gation also plays a vital role in electrochemical performance. In the case of carbon black, 84,85one parameter to characterize the agglomerate of primary carbon black particles, namely, the adsorbed amount of dibutyl phthalate (DBP) was correlated with electrochemical properties. The neck positions (where the DBP is adsorbed) connecting two primary carbon black particles in the aggregates have parallel graphitic planes for Li+ intercalation, whereas a primary carbon black particle itself has the concentrically spherical lamellar structure that is unfavorable for Li +inser-tion and diffusion. Other examples for the aggregate structure are the composite electrode such as graphite + carbon (acetylene) black, 39,86carbon fibers bound by carbonized epoxy resin, 87graphite coated with carbon (core–shell structure), 88–90or in some carbon fibers, two different textures coexist with one single fiber. 833.4 Li +Diffusion in CarbonS ince the slow solid-state diffusion of Li +in the bulk of carbon may control the rate-determining step of the intercalation process and consequently affect the powerdensity of Li +-ion batteries, the chemical diffusion coefficient of Li +( DLi+)becomesa very key kinetic parameter. Several electrochemical relaxation techniques such aspotentiostatic and galvanostatic intermittent titration technique (PITT and GITT, respectively), current pulse relaxation method (CPR), and electrochemical imped-ance spectroscopy have been proposed for calculating D. 91–93The D values might differ by several orders of magnitude, ranging from 10 –6to 10 –13cm 2/S in the pub-lished reports. The accuracy of D values for Li +diffusion in carbon depends on many factors, 94such as carbon structure, potential, surface states of carbon elec-trodes (edge–plane surface effectively exposed to the electrolytes), SEI properties, the measurement techniques, and so forth, which makes it difficult to compare dif-ferent D values evaded different research groups for various kinds of carbon. It was found that the activation energy for Li +diffusion process in soft carbon decreaseswith an increase of the graphitization degree given the same x value in Li x C6.95Incontrast, micropores and defects in disordered carbon can retard Li +diffusion and enhance the activation energy. 96The relationship between D values and Li +inser-tion content in carbon has become a focused interest of some research groups. 97–100 Investigations on ultrathin film or single particles of graphitic carbons found that the plots of D vs. the lithiation degree in graphite demonstrate three marked minima located at just the same potentials in which cyclic voltametries show the peaks that correspond to phase transitions of Li +-graphite intercalation stages, for example, as shown in Fig. 3.7 .F ig. 3.7C yclic voltammogram and the diffusion coeffecient of Li +in graphite vs. potential. Reprinted from, 101copyright (1997) with permission from Elsevier Ltd3.5 Carbon with Extra-High CapacityR ecently, much enthusiasm and effort have been concentrated on the development of high-capacity carbonaceous materials that are synthesized at relative low temperatures (from 500 to 1,100°C) and deliver reversible capacities over 372 mAh/g. To rationalize the “extra” lithium storage capacity, a variety of models and explanations have been suggested.S awai et al. assumed that the high-capacity carbons offer high volume for lithium accommodation, thus only the gravimetric capacity is higher than that of graphite 102; Yazami et al. proposed the formation of lithium multilayers on the graphene sheets 103; Peled et al. believed that the extra capacity by mild oxidation of graphite is attributable to accommodation of lithium at edge planes between two adjacent crystallites and in the vicinity of defects and impurities 104; Sato et al. suggested that lithium occupies the nearest neighbor sites in interca-lated carbons 105; Osaka research group proposed that extra lithium resides into nano-sized cavities 106–108; Yata et al. discussed the possibility of the formationof LiC2in “polyacenic semiconductor” carbons with high interlayer distance( ~0.400 nm) 109; Matsumura et al. assumed that small particle-sized carbons can store considerable amounts of lithium on graphite edges and surfaces in addi-tion to the lithium intercalated between graphene layers 110; and Xiang et al. ascribed the plateau at about 1 V vs. Li/Li +to the lithium doped at the edges of graphene layers. 111D ahn and his collaborators have carried out systematic studies on carbon lithia-tion in detail. 112They gave a comprehensive set of explanations for high lithium storage capacities in disordered carbons. In the case of both the soft and hard car-bons heated below 800°C, large capacities as well as large hysteresis could be obtained. 113,114The hysteresis capacity is proportional to the hydrogen content in carbon, so that lithium is somehow bound near the hydrogen. 115Inaba et al. has investigated the thermal behavior of low-temperature-treated MCMB during charge-discharge cycling. 116The large hysteresis in a voltage profile is accompa-nied by the large exotherms. This phenomenon was explained in terms of the activation energy barrier, which is in agreement with the above proposal of lith-ium–hydrogen interactions. As the heating temperature rises, hydrogen is depleted from carbon. The achieved capacities after removal of hydrogen depend mainly on the crystal structure of resulted carbon. Soft carbons heated at tempera-tures higher than 1,000°C have a lot of turbostratic disorders, so that the capaci-ties are lower than 372 mAh/g. With the rise of heating temperature, graphitization proceeds and the fraction of ordered-stacking graphitic layers increases, so the capacity will increase and approach the value of 372 mAh/g. In contrast, hard carbons obtained near 1,000°C show little hysteresis and deliver capacity exceeding 372 mAh/g at a low potential of a few mV vs. Li/Li +.117,118Dahn suggested lithium is “adsorbed” on both sides of the single-layer sheets that are arranged like a “house of cards.” 1193.6 Thermal Safety of Lithiated CarbonMost abusive conditions like short-circuit, crushing, nail-piercing, overcharge/discharge, and so forth will lead to heating of the batteries. Safety problems arise if the batteries exceed a critical temperature, above which thermal runaway occurs.So the thermal stability of the entire Li +-ion battery and various combinations of battery components are necessary for understanding and improving battery safety.Accelerating rate calorimetry (ARC) 58, 59, 120– 122 and differential scanning calorimetry(DSC) 57, 123 are generally used to investigate the causes of thermal run away in Li x C . The ARC is a sensitive adiabatic calorimeter which tracks the temperature change of reactive samples as they self-heat. In ARC studies, temperatures of the samples and calorimeter are increased to an initial temperature at first, and then the adiabatic self-heating rate of the sample is monitored. ARC studies demonstrated that self-heating of Li x C 6 depends on at least four factors: initial lithiation degree, the electrolyte, surface area of carbon, and initial heating temperature of the sample. The conversion of the metastable SEI components to stable SEI produce a peak in the self-heating rate profile and the intensity of this peak becomes larger with the increase in carbon surface area. Richard and Dahn have proposed a mathematicalmodel of reactions generating heat in Li x C 6 samples in the electrolytes. 124They used this model to calculate the self-heating rate profiles as well as DSC curves(DSC is performed at a fixed heating rate). DSC studies suggested that at first there is an exothermic reaction between 120 and 140°C, which comes from the transfor-mation of the metastable SEI film components into LiF and LiC 2O 3 . On further heating, Li x C 6 reacts with the molten PVDF binder via dehydrofluorination near 200°C. The former reaction depends strongly on the surface area of the carbon and is a linear function of the initial irreversible capacity. The latter reaction depends on PVDF content, lithiation degree, as well as specific surface area of carbon.T o improve the safety of Li +-ion batteries, some efforts also have been focused on the development of nonflammable electrolytes. One easy approach is the addi-tion of fire retardants into the electrolytes. 125– 1303.7 Structure Modification of CarbonI n the early stage of the research field of carbons as anode materials for Li +-ion batteries, most work was devoted to the search for carbon suitable for Li +-ionbatteries’ anode materials. This fact is partly due to the diversity of carbon materials and their multifaceted properties. With the development of the studies, deeper, more comprehensive insights have been gained in understanding the key factors that control carbon’s electrochemical performance. The enriched knowledge of carbon lithiation helps battery researchers design and modify carbons to meet thepractical needs in Li +-ion batteries. In turn, during the course of “processing”。

锂离子电池英语论文

Octadecylamine oxide as the template synthesis of lithiated vanadium oxides half opened- nanotubesSynthesis of Lithiated Vanadium Oxides Half Opened- nanotubes as CathodeMaterials for Lithium Ion BatteriesJunli Sun*In stitute of Science and Research, Departme nt of Scie nee and Research, Chin ese People ' s Armed Police Force Academy, 220 Xihuan Road, Anci District, Langfang City, Hebei Provi nee (065000), Chi na. Tel (86)316-2067617AbstractThe lithiated van adium oxides half ope ned- nano tubes (HOT) are syn thesized by using solid-state and solvothermal react ion with octadecylam ine oxide as the template. Transmission electron microscopy (TEM) and scanning electron microscopy (SEM) characterizati ons show that the syn thesizedlithiated van adium oxides nano tubes are half ope ned and agglomerate. X-ray diffractio n (XRD) inv estigatio n dem on strates that the synthesizedhalf opened-nanotubesare most consisted of monoclinic phase LiV 3O8. Cyclic voltammetry (CV) test indicates that some redox processes are hindered, which is propitious to improve electrochemical performanee of LiV 3O8 cathode material.Keywords:electrochemical properties; nano structures; SEM; TEMIntroductionNano structured cathode and anode materials in lithium ion batteries have attracted*Correspo ndi ng author. Tel.: +86-316-2067617; Fax:+86-316-2067613E-mail addresses: sunj un li @nan .c ngreat atte nti on. This is because they show higher capacity tha n conven ti onalelectrodes composed of the same materials, and the surface area of nanostructured electrodes is much larger than that of conventional electrodes. Vanadium oxides have been widely studied as cathode active materials in lithium rechargeable batteries because of their low cost and high theory capacity [1-6]. Chen W et al. use the template hydrothermal treatment to synthesize V2O5 nanotubes. When they are used as cathode, the resulting cell has shown initial discharge specific capacity of 306mAh -1 g at 3.6-1.5V, which is significantly superior to that of materials prepared by conventional methods. This nanotube can maintain 80% of its initial capacity [7]. But there were no reports about any methods to process LiV 3O8 half opened-nanotubes electrode material. In this work, high-ordered LiV 3O8 half opened- nanotubes arrays are synthesized by using The solid-state and solvothermal reaction with octadecylamine oxide as the template.Octadecylamine (18胺)Cetyltrimethylammonium bromide(CTAB)2 ExperimentalAll of the chemical reagents were of analytical grade and used without furtherpurification. 1. V2O5 (0.06 mol) was added to 25 ml 30% (w/w) H2O2 aqueous solution,and the resulting mixture was stirred for 2 h. Then, 0.04 mol mixtures(LiOH H2O and AgNO3 with different mol ratios) were added in a desired stoichiometricratio, together with 15 ml of 1 mol/L HNO3 aqueous solution. PH measurement isperformed with a pH meter using 2.4 for calibration.After continuous stirring for 2 hours, the resulting precursor suspension wastransferred into a 100 mL Teflon-lined autoclave and maintained at 180C for a certain time. After being cooled to ambient temperature naturally, thesolution in the autoclave was collected and finally vacuum-dried at 100 C for 12 h. F inal°ly the solid powder was calcined at certain temperatures for 16 hours. For comparison, without hydrothermal route, LiV 3O8 particles were also calcined at 400 C for 16 hou°rs. 2.2. Measurements The composite cathodes (mg/cm2) were prepared by pressing the mixture of the active materials, conductive material (acetylene black) and binder (PTFE) in a weight ratio of 8/1/ 1. The Li metal was used as the counter and reference electrodes. The electrolyte was 1 M LiPF6 in a 6/3/1 (volume ratio) mixture of ethylene carbonate (EC), propylene carbonate (PC) and dimethyl carbonate (DMC). The galvanostatic method was employed to measurethe electrochemical capacity of the samples at a -1current density of 60mAg , with the same cut-off voltages (1.8-4.0 V) for charge and discharge processes, respectively. All tests were performed at room temperature X-ray powder diffraction (XRD) was carried out using XRD (D/Max-2500). Scanning Electron Microscopy (SEM) measurements were carried out on a Hitachi S-570 microscope. CHI 660b electrochemical workstation was used to test Cyclic -1 voltammetry (CV) (sean rate: 0.1 mVs , cut off voltage: 1.8 F.O V) measurements.Fig.I.SEM and TEM images of LiV 3O8 half ope ned- nano tubesFig.lshows the morphology of LiV 3O8 half ope ned- nano tubes. For the LiV 3O8 half ope ned- nano tubes powders,Nano tubes are clearly observed on the surfaces of LiV 3O8 particles. The morphology of 1.0 wt. % LiV 3O8 half ope ned- nano tubes and 2.0 wt. % LiV 3O8 half ope ned- nano tubes are much differe nt to bare_iV 3O8. LiV 3O8 particles are coated by AIPO4 nano wires uni formly at 1.0 wt. % AlPO 4 coat ing. When the coati ng amount in crease to 2.0 wt. %, many AIPO4 nano wires can be observed on the surface ofLiV 3O8 particles, but it also can be found that some AIPO4 compound is formed as little particles. In the case of the 3.0 wt. % AIPO4 coat in g, LiV3O8 particles were coated mainly by AIPO4 particles and only few AIPO4 nano wires can be observed. Its morphology is similar to bare LiV 3O8. The reason is that too much concentration of the AIPO4- nan oparticle soluti on will not be propitious to formatio n of AIPO4 nano wires. It has bee n reported by many researchers that surfacemorphology is an importa nt factor for electrochemical performa nces of LiV3O8.The TEM micrographs of 1.0 wt. % LiV 3O8 half ope ned- nano tubes is show n inFig.3. AIPO4 coated on its surface prese ntsa well nano wires (about ① 40 nm and 0.5~2 卩mlong) morphology. One end of AIPO4 nano wires is outward and visible, while ano ther end of it is in visible and in tegrates into LiV3O8 matrix. AIPO4 will partillay react with LiV3O8 to form a solid solution in the surface of LiV3O8 matrix. Compositi on in Fig.3c is con firmed by the EDX spectrum in Fig.3d. The Cu and C eleme nts are attributed to Cu foil. The atomic ratio of Al/P is 1.1:1 approximate to theoretical value.Fig.1. XRD patter ns LiV3O8 half ope ned- nano tubesFig.2 shows the X-ray diffractio n (XRD) patter ns of the five powders syn thesizedby sol-gel methods. From XRD an alyses, all samples are found to be almost in sin gle phase form.lt is show n that all the peaks are in accorda nee with the patter ns ofLiV3O8. So it is suggested that Ag assuredly en ters the san dwich structure, the Ag doped sample is not just a composite of the Ag metal and LiV3O8 phase. The main differe nce is the relative in ten sity of the d oo peaks. It is found that there are only weak X-ray diffraction peaks of Ag x Li 1-X V3O8 (x= 0.02, 0.04, 0.06, 0.08) observed, and therelative intensity of the X-ray diffraction pattern of the LiV3O8 powder is the stron gest of all. Accordi ng to K,West[8], the low inten sity of the d100 peak in dicates that the dimensions of the crystallites in the plane are relative small and the crystallizati on is beco ming weak. In other words, this con diti on is propitious to improve the electrochemical performa nce of the van adium oxide cathode materials.nwarlna^lucVoltagelV4.00 50 100 150 200 250 300 350Specific Capacity /mAhg-1[1] D.B. Le, S. Passerini, F. Coustier, J. Guo, T. Soderstrom, B.B. Cwens, W.H. Smyrl, Chem Mater. 10 (1998) 682.[2] S. Okada, J. Yamaki. Extended Abstracts of the 176th Meeting of the Electrochemical Society; Hollywood, CA, 15-20 Oct, P62,1989.[3] J.M. Cocciantell, M. Menetrier, C. Delmas, J.P. Doumerc, M. Pouchard, M. Broussely, J. Labat , Solid State Ionics. 78 (1995) 143.[4] Y. Sakurai, J.I. Yamaki, J Electrochem Soc. 135 (1988) 791.[5] M.G. Minett, J.R. Owen, J Power Sources. 32 (1990) 81.[6] J.M Cocciantell, Brousely M, Doumerc JP, Labat J, Poachard M. J Power Sources.34 (1991) 103.3.53.0 -2.52.0 -1.5 +-504.0[7] W. Chen, J. Peng, L. Mai, H .Yu, Y. Qi, Chem Lett. 33 (2004) 1366.。

[课外阅读]前景广阔的锂离子二次电池

[课外阅读]前景广阔的锂离子二次电池锂二次电池是本世纪90年代新发展起来的绿色能源。

也是我国能源领域重点支持的高新技术产业，以其高可逆容量、高电压、高循环性能和高能量密度等优异性能而备受世人青睐，被称为20世纪的主导电源，其应用领域不断扩大，目前已由3C市场（Consullle，COpe。

dCommunicabo扩大至4THCCORDLESST00LS，无绳工具）市场。

迅速对电池市场发起冲击，大有独瞩天下之势，产值也多达30多亿美元。

因此，作为键二次电池负极材料的中间相沥青炭微球（MesocalbonMicmbeads．MC皿B）必将随着理二次电池业的兴旺而更具光明的前景。

所谓中间相沥青炭微球，就是沥青类有机化合物经液相热缩聚反应形成的一种微米级的各向异性球状炭物质，具有密度高、强度大、表面光滑和结构上呈层状有序排列等特点．是银离子二次电池鱼极的首选材料。

另外，这种中间相炭微球由于其自身烧结性，因而可不加任何填料而直接制造高密高强的各向同性炭块，其力学性能、抗摩擦性能及各向异性指标均优于普通炭块；同时可将多种有机官能团引人球体表面而作为离子交换或高效液相色谱往的填充材料；还有炭微球经过适当的活化处理后，可容易地制得比表面积达协4000M/&的超级活性炭材料（其比表面积和吸附能力远远超过现有任何活性炭物质，如活性炭纤维和球状活性炭等），而且这种活性炭材料具有某些分子筛的性质（发达的微孔结构），既具有可控制的粒径分布，又具有高孔隙体积和高吸附容量，不但可以作为催化剂的载体材料及高级吸附材料，而且还可在临床医学上用作血液过的剂及天然气汽车的储藏甲烷材料等，应用领域极为广阔。

尽管日本已于80年代末就实现了中间相沥青炭微球的产业化生产，但仍存在着收率低、球形度差、制备工艺复杂等缺陷，尤其是目前将中间相沥青炭微球作为理二次电池电极材料使用时，都要进行2800℃石墨化处理，这无疑大大提高了中间相沥青炭微球的制备成本，极不利于广泛的使用。

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