Characterization of high-power lithium-ion batteries by electrochemical

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锂电池随使用而最大容量下降的原因

锂电池随使用而最大容量下降的原因

锂电池随着使用次数增加而最大容量下降将分为内因和外因来说:1.内因(1)在电极方面,反复充放电使电极活性表面积减少,电流密度提高,极化增大;活性材料的结构发生变化;活性颗粒的电接触变差,甚至脱落;电极材料(包括集流体)腐蚀;现阶段常用电池负极为石墨,正极是LiCoO2,LiFePO4以及LiMn2O4等,电池放点初期电解液会在电极表面形成一层SEI(固态电解质)膜,其成分主要是ROCO2Li(EC和PC环状碳酸酯还原产物)、ROCO2Li和ROLi(DEC和DMC等链状碳酸酯的还原产物)、Li2CO3(残余水和ROCO2Li反应产物),若用LiPF6时,残余的HF会与SEI中ROCO2Li,使SEI中主要是LiF和ROLi。

SEI是Li+导体,脱嵌锂时碳电极体积变化很小,但即使很小,其产生的内应力也会使负极破裂,暴露出来新的碳表面再与溶剂反应形成新的SEI膜,这样就造成了锂离子和电解液的损耗,同时,正极材料活性物质膨胀超过一定程度也会形成无法修复的永久性结构触损耗,这样正极和负极的不断损耗造成了容量的不断衰减;再者,增加的SEI膜会造成界面的电阻层架,使电化学反应极化电位升高,造成电池性能衰减在电极中,随着充放电反应的进行,黏结剂的性能也会逐步下降,,黏结强度降低,使电极材料脱落;铜箔和铝箔是常用的负极和正极集流体,两者都容易发生腐蚀,腐蚀产物聚集在集流体表面成膜,增加内阻,铜离子还能形成枝晶,穿透隔膜,使电池失效。

(2)在电解质溶液方面,电解液或导电盐分解导致其电导率下降,分解物造成界面钝化;锂离子电池液体电解质一般由溶质(如LiPF6、LiBF4、LiClO4等锂盐)、溶剂和特种添加剂构成。

电解质具有良好的离子导电性和电子绝缘性,在正负极之间起着输送离子传导电流的作用。

锂离子电池在第一次充放电、过充和过放时以及长期循环之后,电解质会发生降解作用,并伴有气体产生,气体的组成较为复杂,还无法通过某种反应在电池内加以消除。

锂电池正极材料和前驱体

锂电池正极材料和前驱体

锂电池正极材料和前驱体Lithium-ion batteries play a crucial role in powering many of our electronic devices, from smartphones to electric vehicles. One of the key components of these batteries is the positive electrode material, which is responsible for storing and releasing lithium ions during charge and discharge cycles. The development of high-performance positive electrode materials is essential for improving the energy density, power output, and lifespan of lithium-ion batteries.锂离子电池在许多电子设备中发挥着至关重要的作用,从智能手机到电动汽车。

其中一个关键组件是正极材料,它在充放电周期中负责储存和释放锂离子。

高性能正极材料的开发对于提高锂离子电池的能量密度、功率输出和寿命至关重要。

There are various types of positive electrode materials that have been investigated for lithium-ion batteries, including lithium cobalt oxide (LiCoO2), lithium iron phosphate (LiFePO4), and lithium nickel manganese cobalt oxide (LiNixMnyCozO2). Each material has its own unique set of characteristics, such as energy density, cycling stability,and cost. Researchers are continuously exploring new materials and formulations to improve the performance of lithium-ion batteries.有各种类型的正极材料被研究用于锂离子电池,包括氧化钴锂(LiCoO2)、磷酸铁锂(LiFePO4)和氧化镍锂锰钴(LiNixMnyCozO2)。

锂离子电池基础科学问题(Ⅷ)——负极材料

锂离子电池基础科学问题(Ⅷ)——负极材料

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with improved reversible capacity and cyclicstability for lithium ion batteries 2010(18)225.Wang Y;Zhang L Simple synthesis of CoO-NiO-C anode materials for lithium-ion batteries and investigation on its electrochemical performance 2012226.Zhang P;Guo Z;Kang S Three-dimensional Li2O-NiO-CoO composite thin-film anode with network structure forlithium-ion batteries 2009(1)227.Zhu X J;Guo Z P;Zhang P Highly porous reticular tin-cobalt oxide composite thin film anodes for lithium ion batteries 2009(44)228.Wang C;Wang D;Wang Q Fabrication and lithium storage performance of three-dimensional porous NiO as anode for lithium-ion battery 2010(21)229.Xia Y;Zhang W;Xiao Z Biotemplated fabrication of hierarchically porous NiO/C composite from lotus pollen grains for lithium-ion batteries 2012(18)230.Yu Y;Chen C H;Shi Y A tin-based amorphous oxide composite with a porous,spherical,multideck-cage morphology as a highly reversible anode material for lithium-ion batteries 2007(7)231.Li F;Zou Q Q;Xia Y Y Co-loaded graphitable carbon hollow spheres as anode materials for lithium-ion battery 2008(2)232.Wu Z S;Ren W;Wen L Graphene anchored with Co3O4 nanoparticles as anode of lithium ion batteries with enhanced reversible capacity and cyclic performance 2010(6)引用本文格式:罗飞.褚赓.黄杰.孙洋.李泓.LUO Fei.CHU Geng.HUANG Jie.SUN Yang.LI Hong锂离子电池基础科学问题(Ⅷ)——负。

High-powerlithiumbatteriesfromfunctionalizedcarbon-nanotubeelectrodes

High-powerlithiumbatteriesfromfunctionalizedcarbon-nanotubeelectrodes

High-power lithium batteries from functionalized carbon-nanotube electrodesSeung Woo Lee 1†,Naoaki Yabuuchi 2†,Betar M.Gallant 2,Shuo Chen 2,Byeong-Su Kim 1,Paula T.Hammond 1and Yang Shao-Horn 2,3*Energy storage devices that can deliver high powers have many applications,including hybrid vehicles and renewable energy.Much research has focused on increasing the power output of lithium batteries by reducing lithium-ion diffusion distances,but outputs remain far below those of electrochemical capacitors and below the levels required for many applications.Here,we report an alternative approach based on the redox reactions of functional groups on the surfaces of carbon yer-by-layer techniques are used to assemble an electrode that consists of additive-free,densely packed and functionalized multiwalled carbon nanotubes.The electrode,which is several micrometres thick,can store lithium up to a reversible gravimetric capacity of ∼200mA h g 21electrode while also delivering 100kW kg electrode 21of power and providing lifetimes in excess of thousands of cycles,both of which are comparable to electrochemical capacitor electrodes.A device using the nanotube electrode as the positive electrode and lithium titanium oxide as a negative electrode had a gravimetric energy ∼5times higher than conventional electrochemical capacitors and power delivery ∼10times higher than conventional lithium-ion batteries.Amajor challenge in the field of electrical energy storage is to bridge the performance gap between batteries and electroche-mical capacitors by developing materials that can combine the advantages of both devices.Batteries exhibit high energy as a result of Faradaic reactions in the bulk of active particles,but are rate-limited.Electrochemical capacitors 1–3can deliver high power at the cost of low energy storage by making use of surface ion adsorption (referred to as double-layer capacitance)and surface redox reactions (referred to as pseudo-capacitance).Lithium rechargeable batteries ( 150W h kg cell 21and 1kW kg cell 21)therefore have higher gravimetric energy but lower power capability than electrochemical capacitors ( 5W h kg cell 21and 10kW kg cell 21)1.Energy and power versatility are crucial for hybrid applications 2.For example,although conventional batteries have been used in light vehicles,hybrid platforms for heavy vehicles and machineries demand delivery of much higher currents,so higher energy and comparable power capability relative to electrochemical capacitors are needed to meet this demand 1,2.Considerable research efforts have been focused on increasing the power characteristics of lithium rechargeable batteries by redu-cing the dimensions of lithium storage materials down to the nano-metre scale 4–12,which would reduce the lithium diffusion time that accompanies the Faradaic reactions of active particles.However,nanostructured lithium storage electrodes 5,13still have a lower power capability than electrochemical capacitor electrodes.On the other hand,researchers have shown that the gravimetric energy of electrochemical capacitors can be increased by using electrode materials with enhanced gravimetric capacitances (gravimetric charge storage per volt),which can be achieved through the use of carbon subnanometre pores for ion adsorption 1,14or by taking advantage of the pseudocapacitance of nanostructured transition metal oxides 15–17.The high cost of ruthenium-based oxides is prohibitive for many applications,and the cycling instability of manganese-based oxides 17–19remains a major technical challenge.A promising approach is to use the Faradaic reactions of surface functional groups on nanostructured carbon electrodes,which can store more energy than the double-layer capacitance on convention-al capacitor electrodes 1and also provide high power capability.Here,we report the use of an entirely different class of electrodes for lithium storage,which are based on functionalized multiwalled carbon nanotubes (MWNTs)that include stable pseudo-capacitive functional groups,and are assembled using the layer-by-layer (LBL)technique 20.These additive-free LBL-MWNT electrodes exhibit high gravimetric energy (200W h kg electrode 21)delivered at an exceptionally high power of 100kW kg electrode 21in Li /LBL-MWNT cells when normalized to the single-electrode weight,with no loss observed after completing thousands of cycles.LBL-MWNT electrodes show significantly higher gravimetric energy not only over electrochemical capacitor electrodes,but also over high-power lithium battery electrodes,with gravimetric powers greater than 10kW kg electrode 21.In addition,cells (analogous to asymmetric electrochemical capacitors)consisting of LBL-MWNTs and a lithiated Li 4Ti 5O 12(LTO)negative electrode have comparable gravimetric energy to LTO /LiNi 0.5Mn 1.5O 4cells 21at low gravimetric power,but can also deliver much higher energy at higher power.Gravimetric energy and power at the cell level may be estimated by dividing these values based on LBL-MWNT weight by a factor of 5(ref.22).Furthermore,we show that the Faradaic reactions between the lithium ions and the surface functional groups on the MWNTs are responsible for the high gravimetric energy found in Li /LBL-MWNT and LTO /LBL-MWNT cells.Physical characteristics of LBL-MWNT electrodesStable dispersions of negatively and positively charged MWNTs were obtained by functionalization of the exterior surfaces with car-boxylic-acid (MWNT–COOH)and amine-containing (MWNT–NH 2)groups,respectively 23.Uniform MWNT electrodes on glass1Department of Chemical Engineering,Massachusetts Institute of T echnology,Cambridge,Massachusetts 02139,USA,2Department of Mechanical Engineering,Massachusetts Institute of T echnology,Cambridge,Massachusetts 02139,USA,3Department of Materials Science and Engineering,Massachusetts Institute of T echnology,Cambridge,Massachusetts 02139,USA;†These authors contributed equally to this work.*e-mail:shaohorn@coated with indium tin oxide (ITO)(Fig.1a)were assembled by alternate adsorption of charged MWNTs 23.Electrode thickness increases linearly with the number of positively and negatively charged layer pairs (bilayers),as shown in Fig.1b.The transparency of the MWNT films decreased linearly with increasing thickness up to 0.3m m (Fig.1b).The films were then heat-treated sequentially at 1508C in vacuum for 12h,and at 3008C in H 2for 2h to increase film mechanical stability and electrical conductivity bined profilometry and quartz crystal microbalance measurements gave an electrode density of 0.83g cm 23(Supplementary Fig.S1)follow-ing the heat treatments,which is one of the highest densities reported for carbon nanotube electrodes 24,25.Cross-sectional scan-ning electron microscope (SEM)images showed that the individual MWNTs were randomly distributed throughout the film thickness,and the MWNT films were uniform and conformal on the substrate (Fig.1c).Moreover,the LBL-MWNT electrodes had an inter-connected network of individual MWNTs (Fig.1c,inset)with well-distributed pores of 20nm,as revealed by transmission electron microscopy (TEM)imaging of an LBL-MWNT electrode slice (Fig.1d).Role of surface functional groups on LBL-MWNTelectrodesX-ray photoemission spectroscopy (XPS)analysis of the LBL-MWNT electrodes after heat treatment revealed that significant amounts of oxygen-containing and nitrogen-containing surface functional groups remained on the nanotube surface.The atomic composition of a representative LBL-MWNT electrode was found to be 85.7%carbon,10.6%oxygen and 3.7%nitrogen (C 0.86O 0.11N 0.04;Supplementary Table S1).The presence of two dis-tinct peaks (531.7+0.1eV and 533.4+0.1eV)in the O 1s spectrum (Supplementary Fig.S2a)could be attributed to oxygen atoms inthe carbonyl groups 26,27and various other oxygen groups (Supplementary Fig.S2c)bound to the edges 26,28of the graphene sheets forming the MWNT sidewalls.High-resolution TEM images of functionalized MWNTs revealed that acid treatments roughened the exterior walls of the MWNTs (Supplementary Fig.S3),exposing carbon atoms on the edge sites.Edge carbon atoms are known to bind with oxygenated species more strongly than carbon atoms in the basal plane 29,which is in good agreement with the XPS finding that more oxygenated species are detected on LBL-MWNT electro-des than on pristine MWNTs.In addition,the chemical environment of the nitrogen atoms in the LBL-MWNT electrodes was mostly in the form of amide groups (Supplementary Fig.S2b),as indicated by the N 1s peak centred at 400.1eV (ref.30).Two small additional peaks in the N 1s spectrum suggest that some nitrogen atoms are pyr-idinic N-6(ref.30)(398.5+0.1eV)and tied in oxidized nitrogen-containing functional groups (402.3eV)30.These surface functional groups can undergo Faradaic reactions,as indicated by the potential-dependent gravimetric capacitance obtained from cyclic voltammetry measurements (Fig.2a).The typical gravi-metric capacitance of LBL-MWNT electrodes in the voltage range 3–4.25V versus Li (with a comparable voltage scale of 0to 1.2V versus standard hydrogen electrode (SHE))is 125F g 21,which is comparable to the values reported for functionalized MWNTs 23,31and porous carbon materials 32,33in aqueous solutions.Reducing the lower potential limit from 3.0to 1.5V led to a significant increase in the gravimetric capacitance from 125to 250F g 21measured at 4.0and 2.5V versus Li.Recent studies have shown that carbonyl (C ¼O)groups can be reduced by Li þand reversibly oxidized in the voltage range from 3.5to 1.5V versus Li in aromatic carbonyl derivative organic materials such as poly(2,5-dihydroxy-1,4-benzoqui-none-3,6-methylene)34and Li 2C 6O 6(ref.35).It is thereforepostulated0.00.51.01.52.02.53.03.5acbdT h i c k n e s s (µm )Number of bilayersFigure 1|Physical characteristics of LBL-MWNT electrodes.a ,Digital image of representative MWNT electrodes on ITO-coated glass slides.The number on each image indicates the number of bilayers (n )in (MWNT–NH 2/MWNT–COOH)n .b ,Thickness of the LBL-MWNT electrodes as a function of the number of bilayers.A linear relationship is apparent for LBL-MWNT electrodes with thicknesses from 20nm to 3m m.Error bars show the standard deviation of the thickness,computed from three samples for each thickness.T ransmittance measured at 550nm as a function of the number of bilayers is shown in the inset.Error bars show the standard deviation of transmittance computed from three measurements.c ,SEM cross-sectional image of an LBL-MWNT electrode on an ITO-coated glass slide after heat treatments.A higher-magnification image is shown in the inset,revealing that MWNT s are entangled in the direction perpendicular to the electrode surface.d ,TEM image of an LBL-MWNT electrode slice,showing pore sizes of the order of 20nm.DOI:10.1038/NNANO.2010.116that the doubled gravimetric capacitance obtained from lowering the lower voltage limit of Li /LBL-MWNT cells (with open-circuit voltages of 3.2V)from 3.0to 1.5V versus Li can be attributed to the Faradaic reactions of surface oxygen on LBL-MWNTs,such as C ¼O LBL-MWNT þLi þþe 2↔C 2OLi LBL-MWNT ,which can become accessible at vol-tages lower than 3V versus Li.The role of surface functional groups in providing high capaci-tances in LBL-MWNTs was further confirmed by comparing the specific capacitance of LBL-MWNTs before and after exposure to 4%H 2and 96%Ar by volume at 5008C for 10h.The gravimetric current and capacitance values of the LBL-MWNTelectrode decreased considerably (by 40%)after this heat treatment,as shown in Fig.2b.XPS analysis showed that this high-temperature heat treatment decreased the amount of surface oxygen and nitrogen functional groups on the MWNTs.The intensities of the distinct C 1s peaks (assigned to carbon atoms in C 2N (ref.36)or C 2O (ref.37)centred at 285.9+0.1eV,carbonyl C ¼O (refs 27,37)groups at 286.7+0.1eV,and amide N 2C ¼O or carboxylic COOR groups at 288.4+0.1eV (ref.36))were greatly reduced (by 70%)relative to those of sp 2(284.5eV)and sp 3(285.2eV)hybridized carbon 37follow-ing heat treatment,as shown in Fig.2c.This experiment therefore pro-vides further evidence that the redox of surface oxygen-containing functional groups with lithium ions is responsible for the large gravi-metric capacitances of LBL-MWNT electrodes in organic electrolytes.The contribution of double-layer capacitance to LBL-MWNT capacitances is relatively small compared to that of Faradaic reactions,and can be estimated by comparing cyclic voltammograms of compo-site electrodes (80wt%MWNTs and 20wt%binder)that include pristine MWNTs with those containing functionalized MWNTs(see Supplementary Information).Composite electrodes with MWNT–COOH and MWNT–NH 2show much higher gravimetric capacitances (factor of 2)than pristine MWNTs (Fig.2d;Supplementary Fig.S4),indicating the dominant contribution from the surface functional groups.In addition,we show that surface func-tional groups on MWNTs are better used in LBL-MWNT electrodes than in composite electrodes.The capacitance normalized to MWNT weight for LBL-MWNT electrodes is 2.5times higher than that of con-ventional composite electrodes (Fig.2d).Considering that the MWNT–COOH and MWNT–NH 2in the composite electrodes have similar ratios of carbon and oxygen atomic percentages as the LBL electrodes (Supplementary Table S1),this result suggests that the binder-free porous network structure of LBL-MWNT electrodes allows better utilization of the surface functional groups than compo-site electrodes with binder,which can block the redox of the surface functional groups.Moreover,the volumetric capacitances of LBL-MWNT electrodes are even greater (by a factor of 5)than those of composite MWNT electrodes because of their higher elec-trode density (0.83g cm 23for LBL-MWNTs versus 0.45g cm 23for composite electrodes).Lithium storage characteristics of LBL-MWNT electrodesThe specific and volumetric capacitances of LBL-MWNT electrodes are greater than those of conventional composite electrodes based on carbon 32,38in organic electrolytes.Because LBL-MWNT electrodes have no additives,the gravimetric capacitance normalized to electrode weight is identical to that normalized to MWNT weight.It is interesting to point out that the gravimetric capacitances of these LBL-MWNT electrodes are comparable to those of12345−1.0−0.50.00.51.0acbdI (A g M W N T −1)I (A g M W N T −1)I (A g M W N T −1)E (V versus Li)−1,000−50005001,0001.48 ± 0.14 µm at 1 mV s −10.31 ± 0.01 µm at 1 mV s −10.31 ± 0.01 µm at 1 mV s −1PVdF-MWNT (pristine)PVdF-MWNT (−NH 2)PVdF-MWNT (−COOH)3.0 −4.25 VBefore 500 °C H 2 treatmentBefore 500 °C H 2 treatment After 500 °C H 2 treatmentAfter 500 °C H 2 treatment4.2 V4.5 V4.5 V4.2 V d Q /d E (F g MWNT −1)d Q /d E (F g MWNT −1)d Q /d E (F g MWNT −1)12345−0.6−0.30.00.30.6−600−300300600E (V versus Li)292290288286284282C 1s LBL-MWNTC−NN−C C−O sp 2−Csp 3−CI n t e n s i t y (a .u .)Binding energy (eV)12345−1.0−0.50.00.51.0−1,000−5005001,000E (V versus Li)−−O−−O COOR C Figure 2|Potential-dependent electrochemical behaviour of LBL-MWNT and functionalized MWNT composite electrodes measured in two-electrode lithium cells.a ,Cyclic voltammogram data for an LBL-MWNT electrode obtained with different upper-and lower-potential limits.Reducing the lower-potential limit from 3to 1.5V versus Li resulted in increased current and gravimetric capacitance.b ,Cyclic voltammogram data for an LBL-MWNT electrode before and after 5008C H 2-treatment in 4%H 2and 96%Ar by volume for 10h.c ,XPS C 1s spectra of an LBL-MWNT electrode before and after this additional heat treatment,which is seen to remove a considerable amount of surface oxygen and nitrogen functional groups from the MWNT surface.d ,Cyclic voltammogram data for an LBL-MWNT electrode and composite electrodes of pristine MWNT,MWNT–COOH and MWNT–NH 2,with the LBL-MWNT electrode having higher current and capacitance normalized to the MWNT weight than the composite electrodes.The composite electrodesconsisted of 20wt%PVdF and 80wt%posite MWNT electrodes were prepared from slurry casting and dried at 1008C for 12h under vacuum.The thickness of the LBL-MWNT electrode was 0.3m m,and the thicknesses of the pristine MWNT,MWNT–COOH and MWNT–NH 2composite electrodes were 40,50and 30m m,respectively.The density of the composite electrodes was 0.45g cm 23.DOI:10.1038/NNANO.2010.116nanostructured composite electrodes with manganese-based oxides ( 40wt%oxides),even though higher capacitances normalized toactive material mass only (for example,up to 600F g MnO221;ref.39)are typically reported.Moreover,taking into account the LBL-MWNT electrode density of 0.83g cm 23,we obtain a volumetric capacitance of 180F cm 23for LBL-MWNT electrodes,which is higher than that of nanostructured carbon ( 50F cm 23)in organic electrolytes 32and nanostructured MnO 2electrodes( 150F cm 23)in aqueous electrolytes 16,40.Very few studies have reported the volumetric capacitance of entire electrodes,and we note that this is,to our knowledge,the highest value reported.Storing energy on the surfaces of MWNTs enables LBL-MWNT electrodes to have a high rate capability.For a given thickness,the current at 3V was found to increase linearly with scan rate from cyclic voltammetry,indicating a surface-redox limited process (Fig.3a,including inset),which is in good agreement with the proposed mechanism of redox of functional groups on MWNT surfaces.LBL-MWNT electrodes were also examined by means of galvanostatic measurements,allowing direct comparison with the performance of high-power battery materials.The gravi-metric capacity of 0.3-m m electrodes was found to be 200mA h g 21at low rates such as 0.4A g 21,which is in good agreement with the estimated capacity of LBL-MWNT electrodes based on the proposed Faradaic reaction between Li and surface oxygen (C 0.86O 0.11N 0.04).Half of the gravimetric capacity (100mA h g 21)was retained at exceptionally high discharge rates of 180A g 21(corresponding to full discharge in less than 2s),as shown in Fig.3b.Moreover,the capacity (stored charge)of LBL-MWNT electrodes increases linearly with electrode thickness (Fig.3c,inset),and a high power capability is maintained with elec-trode thickness increasing to 3m m (Supplementary Fig.S5).The specific energy and power of LBL-MWNTelectrodes with thick-nesses up to 3.0m m,in the 1.5–4.5V range,are shown in Fig.4a (for volumetric energy and power data see Supplementary Fig.S7).Although the powercapabilityof LBL-MWNTelectrodes reduces some-what with increasing thickness,electrodes of 3.0m m can still deliver a very high gravimetric energy of 200W h kg electrode 21at a large gravimetric power of 100kW kg electrode 21,based on single-electrode weight alone.At low powers,their gravimetric energy ( 500W h kg electrode 21)approaches that of LiFePO 4and LiCoO 2(refs 5,35,41;Supplementary Fig.S6).At high powers (greater than 10kW kg electrode 21),LBL-MWNT electrodes show higher gravimetric energy than carbon-nanotube-based electrodes for electrochemical capacitors ( 70W h kg electrode 21;ref.25),thin-film batteries 22,nano-structured lithium battery materials 5,13and high-power lithium battery materials 4,42(Supplementary Fig.S6).As conventional composite electrodes are much thicker than the 3.0-m m LBL-MWNT elec-trodes (.10times),where ion transport in the electrodes can limit power capability,future studies are needed to examine how the power and energy performance of LBL-MWNT electrodes changes with thicknesses up to tens and hundreds of micrometres.LBL-MWNT electrodes can be tested over 1,000cycles without any observable capacity loss,as shown in Fig.4b.Further cycling of a 1.5-m m LBL-MWNT electrode revealed no capacity loss up to 2,500cycles,even after the cell was left open circuit for 30days (Supplementary Fig.S8).The voltage profiles in the first and 1,000th cycles to 4.5V are virtually unchanged (Fig.4c and Supplementary Fig.S8).TEM and XPS analysis of cycled electro-des (1,000cycles to 4.5V,followed by an additional 1,000cycles to 4.7V versus Li)provided further evidence for this cycling stab-ility,with no distinctive change being noted in the surface atomic structure and surface functional groups after cycling (Supplementary Fig.S9).The stability of the functional groups on these MWNTs is remarkable when compared to the consider-able losses of carbonyl derivative molecules within 50to 100cycles reported recently 34,35,43.We hypothesize that the cycling stability of the LBL-MWNT electrodes can be linked to the strong chemical covalent bonding of the surface functional groups on the MWNTs,in contrast to the gradual separation occurring between the active carbonyl groups and carbon addi-tives in composite electrodes during cycling.Because a lithium negative electrode is not practical for real applications,we investigated the use of LBL-MWNT electrodes with a lithiated Li 4Ti 5O 12(LTO)composite electrode (see−1.0−0.50.00.51.0a bE (V versus Li)I (m A )249 A g −1183 A g −137 A g −14.5 V(0.31±0.01 µm)550 A g −12 A g −10.4 A g −16012345E (V v e r s u s L i )E (V versus Li)70140210Q (mA h g −1)Q (µA h)12345−80−404080I (µA )c Figure 3|Electrochemical characteristics of LBL-MWNT electrodes in two-electrode lithium cells with 1M LiPF 6in a mixture of ethylene carbonate and dimethyl carbonate (volume ratio 3:7).a ,Cyclicvoltammogram data for a 0.3-m m LBL-MWNT electrode over a range of scan rates.The current at 3V versus scan rate is shown in the inset.b ,Charge and discharge profiles of an electrode of 0.3m m obtained over a wide range of gravimetric current densities between 1.5and 4.5V versus Li.Before each charge and discharge measurement for the data in Fig.3b,cells were held at 1.5and 4.5V for 30min,respectively.c ,Cyclic voltammogram data forelectrodes with different thicknesses collected at a scanning rate of 1mV s 21in the voltage range 1.5–4.5V versus Li.The integrated charge increases linearly with electrode thickness,as shown in the inset.DOI:10.1038/NNANO.2010.116Supplementary Information).Although the electrode gravimetric energy and power in LTO /LBL-MWNT cells is reduced due to the lower cell voltage (Fig.4d),the rate capability,gravimetric capacity and capacity retention are comparable to cells with a Li negative electrode (Supplementary Fig.S10).Interestingly,although LTO /LBL-MWNT cells show comparable gravimetric energy to LTO /LiNi 0.5Mn 1.5O 4cells at low power,they exhibit significantly higher gravimetric energy at powers greater than10kW kg electrode 21(ref.21;Fig.4d and Supplementary Fig.S11).Using a conservative assumption that the mass of the battery is five times greater than that of the LBL-MWNT 22,which is higher than the 2.5(ref.4)typically used for conventional lithium rechargeable batteries due to reduced electrode thicknesses (such as 3m m)demonstrated in this study,LTO /LBL-MWNT storage devices are expected to deliver 30W h kg cell 21at 5kW kg cell 21.This value is significantly higher than that of current electrochemical capacitors with a gravimetric energy of 5W h kg cell 21at 1kW kg cell 21(refs 1,32).Finally,we show that LBL-MWNT electrodes can also be used in symmetrical LBL-MWNT /LBL-MWNT cells (cell voltage in the range 0–3V).As there is no net Faradaic reaction of surface oxygen-containing functional groups on MWNTs,they exhibit specific capacitances ( 95F g 21)comparable to those (702120F g 21)in electrochemical capacitors reported previously 44,but considerably lower than that of Li /LBL-MWNT cells.Symmetric cells therefore deliver gravimetric energy comparable toconventional electrochemical capacitors 1,32,but lower than Li /LBL-MWNT and LTO /LBL-MWNT cells (Fig.4d).ConclusionsIn summary,LBL-MWNT electrodes,which are conformal,densely packed and additive-free,can exhibit gravimetric energies up to 200W h kg electrode 21at a gravimetric power of 100kW kg electrode 21,where the gravimetric energy and power at the cell level can be estimated by dividing these values by a factor of 5.The energy stored in the LBL-MWNT electrodes can be con-trolled by the electrode thickness (Fig.3c,inset)and upper voltage limit (Supplementary Fig.S12).Redox of surface oxygen-containing functional groups on LBL-MWNT electrodes by lithium ions in organic electrolytes,which can be accessed reversibly at high power,are predominantly responsible for the observed high energy and power capabilities of LBL-MWNT electrodes,as can be seen in the high-resolution TEM (HRTEM)image of the LBL-MWNT elec-trode in Fig.5.We have demonstrated energy and power capabilities of LBL-MWNT electrodes with thicknesses of a few micrometres that will open up new opportunities in the development of high-performance electrical energy storage for microsystems,and flexible,thin-film devices 22.Further research will seek to validate the reported energy and power capabilities of MWNT electrodes with thicknesses of the order of tens and hundreds of micrometres,and minimize energy loss during charge and discharge (charging voltages of LBL-MWNT107a b cd1061054.5 V (1.48 ± 0.14 µm) at 250 mA g −1104103102G r a v i m e t r i c p o w e r (W k g −1)107106105104103102G r a v i m e t r i c p o w e r (W k g −1)Gravimetric energy (W h kg −1)101102103Gravimetric energy (W h kg −1)Q (m A h g −1)Cycle number01st cycle1,000th cycle 102030012345050100150200Q (mA h g −1)E (V v e r s u s L i )Q (µA h)Figure 4|Gravimetric energy and power densities,and cycle life of LBL-MWNT electrodes obtained from measurements of two-electrode cells.a ,Ragone plot for Li /LBL-MWNT cells with different thicknesses ( 0.3–3.0m m).The corresponding loading density of LBL-MWNT electrodes ranges from 0.025–0.25mg cm 22.Only the LBL-MWNT weight was considered in the gravimetric energy and power density calculations.b ,Gravimetric capacities of Li /LBL-MWNT cells as a function of cycle number,measured at a current density of 0.25A g 21once every 100cycles,after voltage holds at the end of charging and discharging for 30min.Within each 100cycles,these cells were cycled at an accelerated rate of 2.5A g 21.c ,Voltage profiles of a 1.5-m m electrode in the first and 1,000th cycles,for which negligible changes were noted.d ,Ragone plot for Li /LBL-MWNT (black squares),L TO /LBL-MWNT (green circles),L TO /LiNi 0.5Mn 1.5O 4(grey circles)and LBL-MWNT /LBL-MWNT (orange triangles)cells with 4.5V versus Li as the upper-potential limit.The thickness of the LBL-MWNT electrode was 0.3m m for asymmetric Li /LBL-MWNT and L TO /LBL-MWNT,and 0.4m m for symmetric LBL-MWNT /LBL-MWNT.Gravimetric energy and maximum power densities were reduced for the L TO /LBL-MWNT cells subjected to the same testing conditions due to a lower cell voltage.DOI:10.1038/NNANO.2010.116electrodes are higher than those on discharge,even at low rates).Large-scale thicker electrodes of tens of micrometres can be produced using a recently developed sprayed LBL system 45that uses an auto-mated process to reduce assembly time dramatically (about 70times faster than the conventional dipping of LBL systems used in this study).Modification of the surface functional groups on carbon 46,47may allow the tuning of redox potentials and increase efficiency by reducing the voltage difference during charge and discharge.MethodsMaterials.MWNTs prepared by chemical vapour deposition were purchased from NANOLAB (95%purity;outer diameter,15+5nm).Carboxylated MWNTs (MWNT–COOH)and amine-functionalized MWNTs (MWNT–NH 2)wereprepared and assembled onto ITO-coated glass slides (procedures are described in detail elsewhere 23).Cross-sectional scanning electron microscope (SEM)images of MWNT electrodes after heat treatments were obtained using a JEOL 6320SEM operated at 5kV.Fabrication of layer-by-layer MWNT electrodes.MWNT–COOH and MWNT–NH 2powder samples were sonicated for several hours in Milli-Q water (18M V cm)to form a uniform dispersion,and this was followed by dialysis using Milli-Q water for several days,resulting in a stable dispersion of functionalized MWNTs in solution (0.5mg ml 21).pH values of the solutions were adjusted to pH 2.5(MWNT–NH 2)and pH 3.5(MWNT–COOH),respectively,and the solutions were sonicated for 1h just before LBL assembly.All-MWNT electrodes were assembled with a modified Carl Zeiss DS50programmable slide stainer.Details of LBLassembly of MWNT electrodes can be found elsewhere 23.Assembled LBL-MWNT electrodes were dried in air,and these films were then heat-treated sequentially at 1508C in vacuum for 12h,and at 3008C in H 2for 2h to increase mechanical stability.X-ray photoelectron spectroscopy (XPS).A Kratos Axis Ultra XPS instrument (Kratos Analytical)with a monochromatized Al K a X-ray source was used to analyse the surface chemistry of functionalized MWNTs and LBL-MWNTelectrodes.The take-off angle relative to the sample substrate was 908.Curve fitting of the photoemission spectra was performed following a Shirley-type background subtraction.An asymmetric C 1s peak from sp 2hybridized carbons centred at 284.5eV was generated for raw ing this asymmetric peak as a reference,all other peaks were fitted by the Gaussian–Lorentzian function.The experimental uncertainty of the XPS binding energy was +0.1eV.The relative sensitivity factors used to scale the peaks of C 1s ,O 1s and N 1s were 0.278,0.780and 0.477,respectively.Electrochemical measurements.Electrochemical measurements were conducted using a two-electrode electrochemical cell (Tomcell)consisting of an LBL-MWNT electrode on ITO-coated glass,two sheets of microporous membrane (Celgard 2500,Celgard)and lithium foil as the counter-electrode.LBL-MWNT electrode areas of 100or 50mm 2were used for electrochemical measurements with Li foil andlithiated LTO negative electrodes.The weights of the LBL-MWNT electrodes were determined from the area and the mass area density (see SupplementaryInformation).The loading density of the LBL-MWNT electrodes ranged from 0.025to 0.25mg cm 22.A piece of aluminium foil (25m m thick and with an areaof 1mm ×7mm in contact with the LBL-MWNT electrode)was attached to one edge and used as a current collector.The electrolyte solution was 1M LiPF 6dissolved in a mixture of ethylene carbonate (EC)and dimethyl carbonate (DMC)with a 3:7volume ratio (3.5ppm H 2O impurity,Kishida Chem.).The separators were wetted by a minimum amount of electrolyte to reduce the background current.Cyclic voltammetry and galvanostatic measurements of the lithium cells were performed using a Solartron 4170at room temperature.Received 26March 2010;accepted 13May 2010;published online 20June 2010References1.Simon,P.&Gogotsi,Y.Materials for electrochemical capacitors.Nature Mater.7,845–854(2008).ler,J.R.&Simon,P.Materials science—electrochemical capacitors forenergy management.Science 321,651–652(2008).3.Amatucci,G.G.,Badway,F.,Du Pasquier,A.&Zheng,T.An asymmetric hybridnonaqueous energy storage cell.J.Electrochem.Soc.148,A930–A939(2001).4.Kang,B.&Ceder,G.Battery materials for ultrafast charging and discharging.Nature 458,190–193(2009).5.Lee,Y.J.et al .Fabricating genetically engineered high-power lithium-ionbatteries using multiple virus genes.Science 324,1051–1055(2009).6.Nazar,L.F.et al .Nanostructured materials for energy storage.Int.J.Inorg.Mater.3,191–200(2001).7.Arico,A.S.et al .Nanostructured materials for advanced energy conversion andstorage devices.Nature Mater.4,366–377(2005).8.Poizot,P.et al .Nano-sized transition-metaloxides as negative-electrodematerials for lithium-ion batteries.Nature 407,496–499(2000).9.Sides,C.R.et al .Nanoscale materials for lithium-ion batteries.MRS Bull.27,604–607(2002).10.Bruce,P.G.,Scrosati,B.&Tarascon,J.M.Nanomaterials for rechargeablelithium batteries.Angew.Chem.Int.Ed.47,2930–2946(2008).11.Tarascon,J.M.&Armand,M.Issues and challenges facing rechargeable lithiumbatteries.Nature 414,359–367(2001).12.Armand,M.&Tarascon,J.M.Building better batteries.Nature 451,652–657(2008).13.Wu,X.L.et al .LiFePO 4nanoparticles embedded in a nanoporous carbonmatrix:superior cathode material for electrochemical energy-storage devices.Adv.Mater.21,2710–2714(2009).14.Chmiola,J.et al .Anomalous increase in carbon capacitance at pore sizes lessthan 1nanometer.Science 313,1760–1763(2006).15.Hu,C.C.,Chen,W.C.&Chang,K.H.How to achieve maximum utilization ofhydrous ruthenium oxide for supercapacitors.J.Electrochem.Soc.151,A281–A290(2004).16.Fischer,A.E.et al .Incorporation of homogeneous,nanoscale MnO 2withinultraporous carbon structures via self-limiting electroless deposition:implications for electrochemical capacitors.Nano Lett.7,281–286(2007).17.Reddy,A.L.M.,Shaijumon,M.M.,Gowda,S.R.&Ajayan,P.M.CoaxialMnO 2/carbon nanotube array electrodes for high-performance lithium batteries.Nano Lett.9,1002–1006(2009).18.Kim,D.K.et al .Spinel LiMn 2O 4nanorods as lithium ion battery cathodes.NanoLett.8,3948–3952(2008).19.Be´langer,D.,Brousse,T.&Long,J.W.Manganese oxides:battery materials make the leap to electrochemical capacitors.Electrochem.Soc.Interf.17,49–52(2008).20.Decher,G.Fuzzy nanoassemblies:toward layered polymeric multicomposites.Science 277,1232–1237(1997).21.Xiang,H.F.et al .Effect of capacity matchup in the LiNi 0.5Mn 1.5O 4/Li 4Ti 5O 12cells.J.Power Sources 183,355–360(2008).22.Dudney,J.N.Thin film micro-batteries.Electrochem.Soc.Interf.17,44–48(2008).23.Lee,Seung Woo et al .Layer-by-layer assembly of all carbon nanotube ultrathinfilms for electrochemical applications.J.Am.Chem.Soc.131,671–679(2009).24.Niu,C.M.et al .High power electrochemical capacitors based on carbonnanotube electrodes.Appl.Phys.Lett.70,1480–1482(1997).25.Futaba,D.N.et al .Shape-engineerable and highly densely packed single-walledcarbon nanotubes and their application as super-capacitor electrodes.Nature Mater.5,987–994(2006).26.Zielke,U.,Huttinger,K.J.&Hoffman,W.P.Surface-oxidized carbon fibers:I.Surface structure and chemistry.Carbon 34,983–998(1996).27.Kozlowski,C.&Sherwood,P.M.A.X-ray photoelectron-spectroscopic studiesof carbon-fibre surfaces.Part 5.The effect of pH on surface oxidation.J.Chem.Soc.Farad.Trans.I 81,2745–2756(1985).28.Frackowiak,E.et al .Electrochemical storage of lithium multiwalled carbonnanotubes.Carbon 37,61–69(1999).29.Zhu,X.Y.,Lee,S.M.,Lee,Y.H.&Frauenheim,T.Adsorption and desorption ofan O 2molecule on carbon nanotubes.Phys.Rev.Lett.85,2757–2760(2000).30.Burg,P.et al .The characterization of nitrogen-enriched activated carbons by IR,XPS and LSER methods.Carbon 40,1521–1531(2002).Surface functional groups:Faradaic RXN centresOOLi Li Li+OO Figure 5|Schematic of the energy storage mechanism of LBL-MWNT electrodes.Faradaic reactions between surface oxygen functional species (orange arrows)and Li schematically illustrated on an HRTEM image of the LBL-MWNT electrodes.Intact graphite layers inside the MWNT s (white arrows)are indicated as electron conduction channels.DOI:10.1038/NNANO.2010.116。

精编版华南理工大学国家级大学生创新训练项目申报书

精编版华南理工大学国家级大学生创新训练项目申报书

华南理工大学国家级大学生创新训练项目申报书国家级大学生创新训练项目申报书项目编号:项目名称:基于ECT的软壳动力电池内部温度场检测装置研制项目负责人:郑国华项目管理学院:机械与汽车工程学院指导教师:洪晓斌华南理工大学教务处二〇一四年四月填写说明1.创新训练项目是本科生个人或团队,在导师指导下,自主完成创新性实验方法的设计、设备和材料的准备、实验的实施、数据处理与分析、总结报告撰写等工作。

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一、基本情况二、立项依据(加页详述)目前已经完成第一阶段工作。

确定出研究方案,将研究内容划分成多个模块,确定各模块任务,分析模块间关系并确定各模块技术指标。

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(1)动力电池组质量在线检测平台(如图2所示),平台包括:OptoNCDT1700传感器2个、S2-1x-02k40 机器视觉传感器2个、V A51-04-C12-0机器视觉图像处理控制器1个、LG5A65PU激光测厚传感器2个、激光测量光幕传感器1套、Compact CI 3A温度传感器1个、D10UNFP塑料光纤传感器1个、EU8电涡流传感器型号1个、PCI6259数据采集卡、三段组合型结构生产线模拟装置、产品在线质量集成测控软件1套、D-LINK DES-1026G1台等。

(2)实验电池对象,图3为10Ah,3.6V的软壳聚合物锂离子电池实验样品(安装电极片)。

(3)动力电池温度检测实验平台(如图4所示),主要包括恒温箱Espec QW1070P6W15(Espec, American) 、温度巡检仪、32通道ECT采集系统、屏蔽电缆及计算机系统等。

前驱体对三元正极材料LiNi_0_省略__Mn_0_3_O_2性能的影响_胡东阁

前驱体对三元正极材料LiNi_0_省略__Mn_0_3_O_2性能的影响_胡东阁

前驱体对三元正极材料LiNi 0.5Co 0.2Mn 0.3O 2性能的影响胡东阁1,王张志1,刘佳丽2,黄桃2,余爱水2*(1.杭州金马能源科技有限公司,浙江杭州311215;2.复旦大学上海市分子催化和功能材料重点实验室,复旦大学化学系,新能源研究院,上海200433)摘要:目前,工业产品的三元正极材料LiNi 0.5Co 0.2Mn 0.3O 2通常使用间接共沉淀和高温固相烧结相结合的方法.共沉淀制得的氢氧化镍钴锰前驱体,其形貌和粒径分布等直接影响着三元材料LiNi 0.5Co 0.2Mn 0.3O 2的性能.使用X 射线衍射(XRD )、扫描电镜(SEM )表征和观察材料晶体结构和表面形貌,并测试粒径分布、振实密度和电化学性能,考察三种前驱体对制得的三元材料的影响.研究结果表明,前驱体的粒径分布直接影响材料的物理性能,表面有大量微孔而又致密的球形是较理想的前驱体形貌;焙烧后可得到结晶度高的材料,0.2C 全电池放电比容量达到156.4mAh ·g -1,循环寿命优异,300周期循环其容量基本不衰减,500周期循环后容量保持率高达92%.关键词:锂离子电池;正极材料;LiNi 0.5Co 0.2Mn 0.3O 2;前驱体中图分类号:O646文献标识码:A锂离子电池具有能量密度高,可以高倍率充放电,循环寿命长等优点,目前正在试用于电动汽车和储能领域[1-2].正极材料是锂离子电池的关键部分之一,钴酸锂是最早应用的正极材料,但是价格高、比容量低、安全性差,所以正极材料一直是研究的焦点.1999年Liu 等[3]提出了Ni-Co-Mn 三元复合锂离子电池正极材料,发现该复合材料由于镍钴锰的协同效应,电化学性能均优于任何单一组分的层状氧化物,较好地兼备了三种组份的优点,弥补了各自的不足,具有比容量高、成本低、循环寿命长及安全性能高等特点[4-8].钴元素能够有效地减弱离子混排,稳定材料的层状结构,提高材料的电导率;镍元素保证材料高容量;锰元素则主要起稳定结构作用.三元材料的理论比容量为277mAh ·g -1,实际比容量可以达到200mAh ·g -1,远高于钴酸锂,被认为是取代钴酸锂的下一代锂离子电池正极材料[7,9-11].目前,工业化三元正极材料LiNi 0.5Co 0.2Mn 0.3O 2通常采用间接共沉淀和高温固相烧结相结合的方法[9,12].间接共沉淀制备的氢氧化镍钴锰前驱体的形貌和粒径分布等因素对三元材料LiNi 0.5Co 0.2Mn 0.3O 2的性能有较大影响,但是关于这方面的研究报道比较少.本文选取了三种不同的前驱体原料,采用相同的中试工艺制得三元正极材料LiNi 0.5Co 0.2Mn 0.3O 2.采用SEM 观察前驱体和三元材料的形貌,XRD 测试材料的微观结构,组装成CR2016扣式半电池和INR26650圆柱全电池测试其电化学性能.1实验1.1LiNi 0.5Co 0.2Mn 0.3O 2的合成三种不同的Ni 0.5Co 0.2Mn 0.3(OH)2前驱体(电池级)工业产品A 、B 和C 作为研究原料.三种前驱体分别各取100kg ,然后分别与440kg 碳酸锂(电池级)进行混合,600o C 预烧7h ,然后再混合,在氧气气氛下900o C 恒温煅烧12h ,冷却,气流粉碎和过筛分级即可得LiNi 0.5Co 0.2Mn 0.3O 2材料.1.2材料物理性能的表征材料的微观晶体结构使用Bruker D8AdvanceX 射线衍射仪分析.Cu/K α辐射源,管压40kV ,管流100mA ,扫描速率2°·min -1,扫描角度2θ范围收稿日期:2012-10-12,修订日期:2012-12-25*通讯作者,Tel:(86-21)51630320,E-mail:asyu@ 上海市分子催化和功能材料重点实验室(No.08DZ2270500)资助电化学JOURNAL OF ELECTROCHEMISTRY第19卷第3期2013年6月Vol.19No.3Jun.2013文章编号:1006-3471(2013)03-0204-06图1三种不同Ni 0.5Co 0.2Mn 0.3(OH)2前驱体A 、B 、C 及相应三元材料A ′、B ′、C ′的SEM 照片Fig.1SEM images of three different precursors (A,B,C)and the corresponding LiNi 0.5Co 0.2Mn 0.3O 2(A',B',C')为10°~80°.使用JEOL JSM-6390型扫描电子显微镜观察材料表面形貌.使用Malvern 2000分析材料的粒径分布.使用智能振实密度仪测试材料振实密度,每分钟振动300次,总共振动3000次,材料质量100g.1.3材料电化学性能测试1)CR2016扣式半电池测试PVDF 先与一定量的NMP (N-甲基吡咯烷酮)溶剂搅拌1h 混成均匀胶状体,然后按照90:5:5的质量比分别称取活性物质LiNi 0.5Co 0.2Mn 0.3O 2,导电剂Super P 和聚偏氟乙烯PVDF.先将活性物质LiNi 0.5Co 0.2Mn 0.3O 2和导电剂Super P 放在研钵中研磨均匀后加入到胶状体中,用机械搅拌器搅拌6h成膏状,用浆料涂布仪将膏状浆料涂到集流体铝箔上,在烘箱90o C 烘干1h ,再置于真空烘箱80o C 烘干12h.专用模具冲压成正极片(准=14mm ),与金属锂片负极、1mol ·L -1LiPF 6溶解在EC/DMC (体积比为1:1)的电解液和Celgard 2300微孔复合隔膜在手套箱无水无氧条件组装成CR2016扣式电池,0.2C 横流充放电测试,电压区间2.5~4.3V.2)全电池3700mAh 的INR26650圆柱电池,按照质量比94:3:3称取活性物质LiNi 0.5Co 0.2Mn 0.3O 2,导电剂Super P 和聚偏氟乙烯PVDF ,经过匀浆、涂布、烘干、滚压、分切、焊极耳、卷绕、底部焊、插入电芯和顶部封口点焊组装成电池,注入电解液和封口即可,电池进行化成后用于测试内阻、充放电、倍率性能和循环寿命.2结果与讨论2.1材料形貌分析图1是三种不同工业产品Ni 0.5Co 0.2Mn 0.3(OH)2前驱体和相应制得的三元材料的电镜图.A 、B 和C 为三种不同工业产品的前驱体,其中B 和C 前驱体较圆滑、规整,且C 前驱体球更圆,并较密实.而A 前驱体球形粗糙,表面不规整、较疏松.焙烧制得三元材料基本保持前驱体的形貌,其中B 和C 经过焙烧后制得三元材料和C ′都为较规整的球形,而从B ′图可以非常清晰看出其有1~2μm 单个小晶体组成,材料结晶度较高,生长比整个晶体较充实饱满.而材料C ′则还是一个整体的球形,结晶性较差,虽可看出晶体生成,但结晶度很低.A 焙烧后所制得材料A ′已经不成球形,但单个晶体结晶度很高,结晶性好,单个晶体为1~3μm.2.2材料晶体结构图2是三个LiNi 0.5Co 0.2Mn 0.3O 2材料的XRD 谱图,从材料的XRD 谱图中可以看出材料都有标准的α-NaFeO 2层状结构,空间群R -3m ,没有杂峰.A ′和B ′两种材料的峰都比较尖锐,说明结晶度较高,(003)/(104)比值大于1.2,(006)/(102)分裂较明显,材料层状结构较完整.而C ′材料的(003)/(104)比值205··电化学2013年小于1.2,(006)/(102)分裂不明显,故材料C ′的结晶度较低,层状结构不甚完整[9,13-14].2.3材料粒径分布和振实密度图3为三种工业产品Ni 0.5Co 0.2Mn 0.3(OH)2前驱体的粒径分布图,表1为相应数据列表.可以看出A 和B 的粒径分布相近,且分布图为正态分布,C的粒径相对小一些.C 的前驱体粒径在0.1~1μm之间,尚存在部分细粉,其可以填充于大颗粒间的小空隙,提高材料的振实密度(2.28g ·cm -3),而A 和B 的振实密度仅为2.22g ·cm -3.焙烧后,A ′和B ′的D 50分别为9.0μm 和9.8μm ,A ′的粒径稍微减小,这可能是组成二次颗粒的一次颗粒在混合和焙烧过程中部分脱落.C ′材料粒径分布变为单峰,且D 10仍为3μm 左右,明显小于A 和B 材料,这是因为其前驱体D 10比较小,存在0.1~1μm 的小颗粒.故C 前驱体所制得材料振实密度最高,达2.51g ·cm -3,A 前驱体所制得材料振实密度最低,仅为2.32g ·cm -3,B 材料为2.42g ·cm -3.A 形貌为不规则的球形,导致材料的振实密度最低.2.4扣式电池电化学性能图4为LiNi 0.5Co 0.2Mn 0.3O 2材料的首次充放电曲线.从图4中可以看出,A 前驱体所制得电极A ′首次放电比容量达到165mAh ·g -1,首次放电效率为87.2%;B 前驱体所制得电极B ′首次放电比容量为163.9mAh ·g -1,首次放电效率为87.9%;而C 前驱体所制得电极C ′首次放电比容量只有157.9mAh·g -1,首次放电效率为86.7%,故C ′电极首次放电比容量最低.图2三种LiNi 0.5Co 0.2Mn 0.3O 2材料(A ′、B ′、C ′)的XRD谱图Fig.2XRD patterns of LiNi 0.5Co 0.2Mn 0.3O 2electrodes (A ′,B ′,C ′)prepared by three differentprecursors图3三种工业产品Ni 0.5Co 0.2Mn 0.3(OH)2前驱体的粒径分布Fig.3Particle size distribution of three different Ni 0.5Co 0.2Mn 0.3(OH)2precursors表1三种工业产品Ni 0.5Co 0.2Mn 0.3(OH)2前驱体粒径分布Tab.1Particle size distribution of three different Ni 0.5Co 0.2Mn 0.3(OH)2precursorsPrecursorParticle size distribution/μmD 10D 50D 90A 5.0529.24016.019B 4.9178.77915.330C2.7675.98110.308206··胡东阁等:前驱体对三元正极材料LiNi 0.5Co 0.2Mn 0.3O 2性能的影响第3期2.5全电池电化学性能INR26650全电池(三种前驱体所制得LiNi 0.5Co 0.2Mn 0.3O 2正极材料,中间相碳微球(CMB )负极)0.2C 放电曲线(3.0~4.2V )如图5所示,B ′电极比容量最高为156.4mAh ·g -1,A ′和C ′电极的比容量为153.0mAh ·g -1左右.从压实密度考虑,A 前驱体制得的材料A ′压实密度最低,只有3.22g ·cm -3;而B 前驱体制得的材料B ′压实密度达到3.31g ·cm -3;C 前驱体制得的材料C ′压实密度达到3.46g ·cm -3.A 材料形貌非常规则,故其制得的材料A ′压实密度较低,而B ′和C ′材料的球形较圆滑.C ′材料压实更高是因其存在着少量的小颗粒,能填充于大颗粒的中间.A ′、B ′、C ′各材料内阻分别为13.1m Ω,12.7m Ω和13.5m Ω.表2列出全电池倍率性能,从表中可以看出B ′电极的倍率性能最好,0.5C 其放电容量为0.2C容量的97.2%,1C 其放电容量为0.2C 的95.24%,3C 其放电容量保持率为94.61%.而A ′电极1C 容量保持率为94.29%,C 材料1C 容量保持率仅为93.24%,这可能归因于其结晶度低.图6给出三种前驱体制得的电极的全电池循图6LiNi 0.5Co 0.2Mn 0.3O 2材料(A ′、B ′、C ′)全电池循环性能曲线Fig.6Cycle performance of LiNi 0.5Co 0.2Mn 0.3O 2electrodes(A ′,B ′,C ′)in fullcell图4三种前驱体制得LiNi 0.5Co 0.2Mn 0.3O 2电极(A ′、B ′、C ′)做成扣式电池首次充放电曲线Fig.4Initial charge-discharge curves of LiNi 0.5Co 0.2Mn 0.3O 2electrodes (A ′,B ′,C ′)prepared by three differentprecursors图5三种前驱体制得LiNi 0.5Co 0.2Mn 0.3O 2电极(A ′、B ′、C ′)全电池放电曲线Fig.5Discharge curves of LiNi 0.5Co 0.2Mn 0.3O 2electrodes(A ′,B ′,C ′)prepared by three different precursors表2全电池倍率性能Tab.2The rate capacity of the full cellSample Capacity/mAh0.2C 0.5C 1C 2C 3C A ′4282.54130.84038.03974.73991.5B ′4179.24062.33980.43933.63953.8C ′4225.24031.53939.43923.23952.5207··电化学2013年环性能.从图6中可以看出,A′电极的循环性能最好,虽前100周期循环其容量下降比较快,但100 ~500周期循环其容量衰减甚小,至500周期循环其容量保持率仍达91.8%,B′电极的比容量在前500周期循环均高于A′电极,据循环寿命曲线的趋势A′电极的比容量在而后循环可能会高于B′电极.C′电极的循环寿命性能较差,其衰减很快,500周期循环其容量仅剩79%.A′材料虽形貌不规整,但其结晶度非常高,而C′材料其结晶度相对较低.3结论前驱体的形貌粒径分布等特性对制得的三元材料的性能有较大影响,前驱体焙烧成三元材料虽仍保持原前驱体的粒径分布,形貌也会影响焙烧后材料的粒径分布,选取适度大小颗粒匹配能提高材料的压实密度,少量适合粒径的小颗粒可填充于大颗粒的间隙.C′材料的压实密度达到3.46 g·cm-3.A前驱体松散,在混料和烧结过程其粒径变小,二次形貌也极不规整,导致其压实密度比较低.但过度致密会导致其与碳酸锂反应不充分,影响材料的结晶度、比容量和循环寿命.前驱体表面有大量微孔而又较致密的球形是比较理想.如B 前驱体焙烧后材料结晶性好、结晶度高,0.2C扣式放电电极比容量达到163.9mAh·g-1,全电池放电比容量达到156.4mAh·g-1,300周期循环其容量基本无衰减,500周期循环其容量保持率还高达92%.参考文献(References):[1]Guo B K(郭炳坤),Xu H(徐辉),Wang X Y(王先友),et al.Lithium ion battery[M].Changsha:Central South Univer-sity Press(中南大学出版社),2002:17-38.[2]Xu J Q,Thomas H R,Francis R W,et al.A review of pro-cesses and technologies for the recycling of lithium-ion secondary batteries[J].Journal of Power Sources,2008, 177(2):512-527.[3]Liu Z L,Yu A S,Lee J Y.Synthesis and characterizationof LiNi1-x-y Co x Mn y O2as the cathode materials of secondary lithium batteries[J].Journal of Power Sources,1999,81: 416-419.[4]Hu C Y,Guo J,Du Y,et al.Effects of synthesis conditionson layered Li[Ni1/3Co1/3Mn1/3]O2positive-electrode via hy-droxide co-precipitation method for lithium-ion batteries [J].Transactions of Nonferrous Metals Society of China, 2011,21(1):114-120.[5]Ohzuku T,Makimura yered lithium insertion materi-al of LiCo1/3Ni1/3Mn1/3O2for lithium-ion batteries[J].Chem-istry Letters,2001,30(7):642-643.[6]Belharouak I,Sun Y K,Liu J,et al.Li(Ni1/3Co1/3Mn1/3)O2asa suitable cathode for high power applications[J].Journalof Power Sources,2003,123(2):247-252.[7]Liang Y G,Han X Y,Zhou X W,et al.Significant im-proved electrochemical performance of Li(Ni1/3Co1/3Mn1/3)O2 cathode on volumetric energy density and cycling stability at high rate[J].Electrochemistry Communications,2007,9(5):965-970.[8]Park S H,Yoon C S,Kang S G,et al.Synthesis and struc-tural characterization of layered Li[Ni1/3Co1/3Mn1/3]O2cath-ode materials by ultrasonic spray pyrolysis method[J].Electrochimica Acta,2004,49(4):557-563.[9]Deng C,Liu L,Zhou W,et al.Effect of synthesis conditionon the structure and electrochemical properties of Li[Ni1/3Co1/3Mn1/3]O2prepared by hydroxide co-precipitation method[J].Electrochimica Acta,2008,53(5):2441-2447.[10]Yang S Y,Wang X Y,Liu Z L,et al.Influence of pre-treatment process on structure,morphology and electro-chemical properties of Li[Ni1/3Co1/3Mn1/3]O2cathode mate-rial[J].Transactions of Nonferrous Metals Society of Chi-na,2011,21(9):1995-2001.[11]Li L J,Li X H,Wang Z X,et al.A simple and effectivemethod to synthesize layered LiNi0.8Co0.1Mn0.1O2cathode materials for lithium ion battery[J].Powder Technology, 2011,206(3):353-357.[12]Zhang S,Deng C,Fu B L,et al.Synthetic optimization ofspherical Li[Ni1/3Co1/3Mn1/3]O2prepared by a carbonate co-precipitation method[J].Powder Technology,2010,198(3):373-380.[13]Kageyama M,Li,D,Kobayakawa K,et al.Structural andelectrochemical properties of LiNi1/3Mn1/3Co1/3O2-x F x pre-pared by solid state reaction[J].Journal of Power Sources, 2006,157(1):494-500.[14]Chang Z R,Chen Z J,Wu F,et al.Synthesis and charac-terization of high-density non-spherical Li[Ni1/3Co1/3Mn1/3]O2 cathode material for lithium ion batteries by two-step dry-ing method[J].Electrochimica Acta,2008,53(20):5927-5933.208··胡东阁等:前驱体对三元正极材料LiNi 0.5Co 0.2Mn 0.3O 2性能的影响第3期The Effect of Precursors on Performance ofLiNi 0.5Co 0.2Mn 0.3O 2Cathode MaterialHU Dong-ge 1,WANG Zhang-zhi 1,LIU Jia-li 2,HUANG Tao 2,YU Ai-shui 2*(1.Hangzhou Golden Horse Energy Tecnology Co.,Ltd.,Hangzhou 311215,China ;2.Department of Chemistry,Shanghai Key Laboratory of Molecular Catalysis and Innovative Materials,Institute of New Energy,Fudan University,Shanghai 200433,China )Abstract:Commercial LiNi 0.5Co 0.2Mn 0.3O 2material is generally prepared by a combination of co-precipitation and solid state re-action method.The particle size distribution and morphology of Ni 0.5Co 0.2Mn 0.3(OH)2precursor have a great impact on the electro-chemical performance of LiNi 0.5Co 0.2Mn 0.3O 2.In this work,the crystal structure and surface morphology of LiNi 0.5Co 0.2Mn 0.3O 2pre-pared by three different precursors were characterized by X-ray diffraction(XRD)and scanning electron microscopy(SEM).Particle size distribution,tap density and electrochemical performance were investigated.The results show that the particle size distribution of every precursor has most direct impact on properties of the corresponding LiNi 0.5Co 0.2Mn 0.3O 2.The precursor with micropores on surface results in the best electrochemical performance.The discharge capacity for full cell test was 156.4mAh ·g -1(0.2C),mean-while,the cycling performance is excellent.The capacity fading was limited in the first 300cycles with up to 92%capacity reten-tion after 500cycles.Key words:lithium ion battery;cathode material;LiNi 0.5Co 0.2Mn 0.3O 2;precursor209··。

锂电池基础科学问题5

锂电池基础科学问题5

第2卷第5期2013年9月 储 能 科 学 与 技 术 Energy Storage Science and Technology V ol.2 No.5Sept. 2013专家讲座锂电池基础科学问题(V )——电池界面郑杰允,李 泓(中国科学院物理研究所,北京 100190)摘 要:电池中固液界面的性质对锂离子电池充放电效率、能量效率、能量密度、功率密度、循环性、服役寿命、安全性、自放电等特性具有重要的影响。

对界面问题的研究是锂离子电池基础研究的核心。

本文小结了 锂离子电池电极表面固体电解质中间相(SEI )形成机理及对其组成结构的认识,介绍了近年来对锂离子输运机制、SEI 膜改性研究以及透射电镜(TEM )及原子力显微镜(AFM )中力曲线等实验技术来分析SEI 膜的形貌、厚度、覆盖度及力学性能等实验方法。

关键词:界面;固体电解质中间相膜;表征;锂离子电池 doi :10.3969/j.issn.2095-4239.2013.05.009中图分类号:O 646.21 文献标志码:A 文章编号:2095-4239(2013)05-503-11Fundamental scientific aspects of lithium batteries (V)——InterfacesZHENG Jieyun ,LI Hong(Institute of Physics ,Chinese Academy of Science ,Beijing 100190,China )Abstract :Interfaces play an important role in determining coulombic efficiency, energy efficiency, energy density, power density, cycle performance, service life, safety and self-discharge rate of lithium-ion batteries. We first briefly summarize our understanding of the formation mechanisms and structure of solid electrolyte interphase (SEI). We then introduce experimental techniques for characterizing the SEI including transmission electron microscopy (TEM), atomic force microscopy (AFM), and TG-DSC-MS.Key words :interface ;solid electrolyte interphase ;characterization ;lithium ion batteries1 锂离子电池界面问题锂离子电池具备优越的综合电化学性能,广泛应用于消费电子领域。

电化学阻抗测量锂电池老化程度

电化学阻抗测量锂电池老化程度

电化学阻抗测量锂电池老化程度Electrochemical Impedance Spectroscopy Testing on the Advanced Technology DevelopmentProgram Lithium-Ion CellsJon P. Christophersen, David F. Glenn, Chester G.Motloch, Randy B. Wright, Chinh D. HoTransportation Technologies and Infrastructure Department Idaho National Engineering and Environmental LaboratoryIdaho Falls, IDVincent S. BattagliaDOE Technical Contact Argonne National LaboratoryWashington, DCAbstract—The U.S. DOE Advanced Technology Development (ATD) Program is investigating Electrochemical Impedance Spectroscopy (EIS) as a new measure of cell degradation. As part of the program, the Idaho National Engineering and Environmental Laboratory (INEEL) is aging 18650-size cells using cycle-life tests developed under the Partnership for a New Generation of Vehicles, which has been superceded by FreedomCAR in January 2002. At beginning of life and every four weeks thereafter, cycle-life testing is interrupted for reference performance tests (RPT) to assess capacity and power fade rates. TheEIS impedance is measured at 60% state-of-charge over a range of frequencies at each RPT. The resulting Nyquist plots show that the two semi-circles, representing the anode and cathode impedance growth, are poorly resolved due to the influence of the high frequency capacitive tail and the low-frequency Warburg impedance. However, impedance growth is clearly visible at the trough frequency of the second semi-circle. The magnitude at this frequency is comparable to the standard measure of cell degradation, which is based on the percent-fade in power as a function of test time while delivering 300 Wh. The percent growth in EIS magnitude at the trough frequency highly correlates with the power fade. This suggests that the EIS test is a useful alternate measure of cell degradation.Keywords—Electrochemical Impedance Spectroscopy; trough frequency; Hybrid Pulse Power Chararacterization test; power fade; Advanced Technology DevelopmentCooperative Automotive Research). Its emphasis will be the development of fuel cell-powered vehicles. “The long-term results of this cooperative effort will be cars and trucks that are more efficient, cheaper to operate, pollution-free, and com petitive in the showroom.”It is believed that advanced high-power batteries will continue to be a critical component in this new program.]II. CELL CHEMISTRYAdvanced Technology Development testing of the second generation of cells (referred to as Gen 2 cells) is now underway. The 18650-size Gen 2 cells consist of a baseline cell chemistry and one variant chemistry (referred to as Variant C). The Baseline cells were manufactured to the following specifications, as developed by Argonne National Laboratory [2]: ?Positive Electrode? 84 wt% LiNi0.8Co0.15Al0.05O2 ? 4 wt% carbon black ? 4 wt% SFG-6? 8 wt% PVDF binder ?Negative Electrode ? 92 wt% MAG-10 ? 8 wt% PVDF binder ? ?Electrolyte? 1.2 M LiPF6 in EC/EMC (3:7 wt%) Separator? 25 μm thick PE CelgardThe Variant C cell chemistry differs from the baseline chemistry by an increase to the aluminum dopant from 5% to 10% and a decrease to the cobalt from 15% to 10% in the cathode (i.e., LiNi0.8Co0.1Al0.1O2). This change resulted in a 20% drop in rated capacity (0.8 Ah) at beginning of life (BOL) compared to the Baseline cell rated capacity of 1.0 Ah. III. CELL TESTINGThe Idaho National Engineering and Environmental Laboratory (INEEL) is cycle-life testing the Gen 2 cells in twoI. INTRODUCTIONThe U.S. Department of Energy (DOE) initiated the Advanced Technology Development (ATD) Program in 1998 to address the outstanding barriers that limit the commercialization of high-power lithium-ion batteries, specifically for hybrid electric vehicle applications. As part of the program, 18650-size cells are aged using calendar- and cycle-life tests developed under the Partnership for a New Generation of Vehicles (PNGV) Power Assist goals. Reference [1] provides additional information about the ATD Program. [Note: In January 2002 at the Detroit Auto Show, Energy Secretary Spencer Abraham announced that PNGV would be superceded by the formation of a new program between the U.S. Government and the U.S. Council for Automotive Research, dubbed FreedomCAR (Freedom0-7803-7467-3/02/$17.00 ?2002 IEEE.1851temperature groups (fifteen Baseline cells at 25°C and fifteen Baseline and Variant C cells each at 45°C), as described in the cell-specific test plan [3]. Cycle-life testing is performed using the PNGV 25-Wh Power Assist profile defined in the PNGV Battery Test Manual, Revision 3 [4]. It consists of a constant power discharge and regen pulse with interspersed rest periods centered around 60% state-of-charge (SOC). The cumulative length of a single profile is 72 seconds and constitutes one cycle. This cycle is repeated continuously during life testing.At BOL and every four weeks (i.e., 33,600 cycle-life profiles) thereafter, cycle-life testing is interrupted for reference performance testing (RPT) which are used to quantify capacity and power fade rates. The RPTs consist of a C1/1 static capacity test, a low-current hybrid pulse power characterization (L-HPPC) test, a C1/25 static capacity test, and an Electrochemical Impedance Spectroscopy (EIS) test. All RPT’s are performed at 25°C. To minimize temperature fluctuations, the cells remain in environmental chambers during testing activities.The C1/1 static capacity test consists of a complete discharge at aC1 rate (i.e., 1.0 A for the Baseline cells and 0.8 A for the Variant C cells) to the minimum voltage from a fully charged cell. The C1/25 capacity test consists of a full discharge and charge at one twenty-fifth of theC1/1 rate (i.e., 40 mA for the Baseline cells and 32 mA for the Variant C cells). These tests are used to track the capacity fade rates as a function of time. The L-HPPC and EIS tests are used to track power fade rates as a function of time. These tests are discussed in detail below.The Gen 2 end-of-test (EOT) criteria are specified in [3]. The INEEL cycle-life cells are organized in three groups of fifteen, as described above. One cell from each group was sent to a diagnostic lab for evaluation after the BOL RPT was completed. Following the 4-week RPT, another two cells were removed from test and sent to diagnostic labs. The EOT criteria for the remaining 12 cells are based on equal powerfade increments such that the penultimate pair of cells are sent for diagnostic evaluation when the power fade reaches 30%. IV. L-HPPC TESTINGThe L-HPPC test is used as the standard PNGV measure of cell degradation. It consists of a constant-current discharge and regen pulse with a rest period in between over a 60-second period. Fig. 1 shows the standard L-HPPC test profile, as specified in [4]. The 18-s constant-current discharge pulse is performed at a 5C1 rate for the ATD Gen 2 cells (i.e., 5 A for the Baseline cells and 4 A for the Variant C cells). This profile is repeated at every 10% depth-of-discharge (DOD) increment, with a 1-h rest at open circuit voltage (OCV) at each DOD increment to ensure that the cells have electrochemically and thermally equilibrated.The BOL L-HPPC test is used to calculate a scaling factor known as the battery size factor (BSF). The BSF is the minimum number of cells required to meet the PNGV power and energy goals (25 kW and 300 Wh, respectively) based on a 30% BOL power margin (i.e., 25 kW * 1.3, or 32.5 kW), as specified in [4]. The 30% BOL power margin enables the cells to simultaneously meet the PNGV power and energygoals as performance degrades over time until the 30% margin is consumed. The BSF is used to scale all subsequent PNGV power and energy-based tests including the 25-Wh Power Assist cycle-life profile [4].The ATD Gen 2 Baseline and Variant C cells require an average BSF of 553 and 651, respectively. Therefore, the Variant C chemistry requires 98 more cells to meet the same power and energy goals as the Baseline cells.1.251.00Current (relative)0.750.500.250.00-0.25-0.50-0.75-1.00102030405060Time in Profile (s)Figure 1. Hybrid pulse power characterization profile.For every RPT, the L-HPPC discharge and regen pulse powers and energies removed at a C1/1 rate are calculated at each 10% DOD increment. This data are used to find the available energy swing over specified discharge and regen power levels [4]. Fig. 2 shows the resulting BSF-scaled available energy versus the BSF-scaled power for a representative Baseline cell cycle-life tested at 45°C for 44 weeks. Cell degradation is measured in terms of power fade, which is the percentloss in power at 300 Wh as a function of test time. For the cell shown in Fig. 2, the initial power at 300 Wh (rightmost curve) is 33.5 kW. Between BOL and 44 weeks, the available energy decreased monotonically with time. At 44 weeks (leftmost curve), the power dropped to 22.4 kW, resulting in a power fade of 33.1%.1800BSF-Scaled Available Energy (Wh)160014001200100080060040020000100002000030000BSF-Scaled Power (W)40000Figure 2. BSF-scaled power versus BSF-scaled energy for a representative45°C Baseline cell.0-7803-7467-3/02/$17.00 ?2002 IEEE.1852Imaginary Impedance (- jZ'')The average power fades as a function of test time for all three INEEL cycle-life groups are summarized in Fig. 3. After 44 weeks of cycle-life testing, the 25 and 45°C Baseline cells show average power fades of 16.0% and 32.1%, respectively. The 45°C Variant C cells show a more rapid power fade of 25.1% after 24 weeks of cycle-life testing. Projections based on power fade rates indicate that the Variant C cells will reach the EOT criteria sooner than the 45°C Baseline cells.Power Fade (%)30%20%10%0%Baseline Cellsfrequency capacitive tail and the low-frequency Warburg impedance. Although they become progressively more distinct as the cell ages, an alternative approach for measuring cell degradation needs to be identified.0.020.0180.0160.0140.0120.010.0080.0060.0040.002000.010.02Real Impedance (ohms)0.03Figure 4. Representative 32-week EIS data with RC network model.Figure 3. Power fade as a function of test timeImaginary Impedance (- jZ'')Baseline CellsINEEL Cell GroupVariant C Cells0.030.02V. EIS TESTINGThe ATD Program is investigating EIS testing as a new measure of cell degradation. The EIS test begins by 0.01discharging the cells from afully charged state to the specified OCV corresponding to 60% SOC. Following an eight-hour rest at OCV, which allows the cells to reach electrochemical equilibrium, the impedance is measured over a frequency 0range of 10 kHz to 0.01 Hz with 10 points per decade of 00.010.020.030.04frequency. INEEL conducts EIS testing with a Model 273AReal Impedance (ohms)EG&G Potentiostat/Galvanostat, a Model 1260 SolartronFrequency Analyzer, and the ZPlot control software. INEELmeasures impedance using a 4-terminal connection, Figure 5. EIS Nyquist plot for a representative Baseline cell after 44 weeks of cycle life testing.eliminating the need to subtract cable impedance.Fig. 4 shows the EIS Nyquist plot after 32 weeks of cycle-life testing at 45°C for a representative ATD Gen 2 Baseline cell. This data can be modeled using four parallel RC networks connected in series. Fig. 4 also shows the outputs of each individual RC network, resulting in four distinct curves. Progressing from left to right, the first curve represents the high frequency capacitive tail (resulting from the 4-terminal connection), which is an artifact arising from apparatus contributions. The anode and cathode primarily influence the first and secondsemi-circles, respectively [5]. The leftmost curve is the Warburgimpedance, which may represent a resistance caused by the diffusion of ions.Fig. 5 shows the EIS Nyquist plot for the same cell shown in Figs. 2 and 4 at each RPT increment from BOL to 44-weeks. Data are only plotted over a frequency range of 2.5 kHz to 0.01 Hz in Fig. 5 to better show the changes in the two semi-circles as a function of test time.The ideal method of measuring cell degradation is to track the growth of these two semi-circles as a function of time. However, as shown in Fig. 5, they are poorly resolved due to the influence of the highThe EIS Nyquist plot can be divided into three different frequency bands (high-, mid- and low-frequency). The break point between the mid- and low-frequency bands is clearly located at the trough frequency. The break point between the high- and mid-frequency is more difficult to identify since the capacitive tail significantly influences the first and second semi-circles. For the analyses discussed in this paper, the break point between the high- and mid-frequency region is guesstimated at 200 Hz.Fig. 6 shows the changes in EIS magnitude as a function of test time at these three different frequency bands for the average of two representative ATD Gen 2 Baseline cells cycle-life tested at 45°C for 44 weeks. Fig. 4 identifies the location of these frequencies on the Nyquist plot. The values shown at “High-Frequency” are the averageimpedance magnitudes at 200 Hz. The mid-frequency delta magnitudes at “Mid-Frequency” are the average magnitudes at the trough frequency minus the average magnitudes at 200 Hz. The values at “Low-Frequency” are the average magnitudes at 500-7803-7467-3/02/$17.00 ?2002 IEEE.1853mHz minus the average magnitudes at 2.5 Hz (the average initial trough frequency). All three frequency bands show some growth over test time. The low-frequency band at 50 mHz showed the smallest percent growth with 7.9% from BOL to 44 weeks. The high-frequency magnitude growth was also small with a 12.3% increase over 44 weeks. The delta magnitude growth at the mid-frequency band showed the most significant growth, with 236.9% from BOL to 44 weeks. Similar results are also seen for the 25°C Baseline cells andthe 45°C Variant C cells.Delta Magnitude (mohms)1412Fig. 8 compares the average EIS magnitude growth at thesemi-circle trough with the average power fade for the INEEL ATD Gen 2 Baseline and Variant C cells. This shows that the magnitude growth is highly correlated with power fade, having R2 values greater than 0.98. The correlation is temperature dependent, with the 25°C Baseline cellsshowing a higher slope than the 45°C cells. The Baseline and Variant C cells tested at 45°C have virtually identical slopes even though the Variant C cells are projected to reach EOT sooner than the Baseline cells. This indicates that the mechanisms responsible for the power fade rate are also responsible for EIS growth.35%30%Power Fade (%)25%20%15%10%5%0%20%40%60%80%1086420High-FrequencyMid-FrequencyFrequenciesLow-FrequencyFigure 6. EIS delta magnitude for an average of two 45°C Baseline cells.0%EIS Magnitude Growth at the Trough(%)Therefore, since the majority of the impedance growth occurs at the mid-frequency band, it can be used to measure cell degradation. However, since the break point between the high- and mid-frequencyband was only guesstimated at 200 Hz, only the EIS magnitude growth at the trough frequency will be considered. For the cell shown in Fig. 5, the 44-week trough magnitude (27.2 m? at 0.5 Hz) grew 63.9% from the BOL trough magnitude (16.6 m? at 2.0 Hz). The average EIS magnitude percent-growth as a function of cycle time for all three INEEL cycle-life groups are summarized in Fig. 7. After 44 weeks of cycle-life testing, the 25 and 45°C Baseline cells show average EIS magnitude growths of 26.2% and 62.1%, respectively. The 45°C Variant C cells show a more rapid magnitude growth with 46.2% after only 24 weeks of cycle-life testing.60%40%20%0%Baseline CellsBaseline CellsINEEL Cell GroupVariant C CellsFigure 8. Magnitude growth at the semi-circle trough frequency versus powerfade.Therefore, the EIS test may be a useful alternate measure of cell degradation. It is a less intrusive alternative to L-HPPC testing since it can be performed at a single SOC and does not require fully discharging the cell at 10% DOD increments. The disadvantage to EIStesting is that no energy calculations are possible. Further studies are required to determine how the correlation between magnitude growth and power fade changes as a function of SOC (all cells shown in Fig. 8 were cycle-life and EIS tested at 60% SOC).VI. CONCLUSIONThe INEEL is cycle-life testing the ATD Gen 2 Baseline and Variant C cells. Every four weeks, cycle-life testing is interrupted for reference performance tests, which include the L-HPPC and EIS tests. From theL-HPPC test, the power fade as a function of test time is tracked as the standard measure of cell degradation. The Nyquist plots show that the majority of the impedance growth occurs at the trough frequency of the second semi-circle. The percent growth in magnitude at that frequency highly correlates with the power fade. This model shows that higher power fade rates also result in higher EIS magnitude growth rates. The model is temperature dependent, with the 25°C Baseline cells showing a higher slope than the 45°C Baseline and Variant C cells. Therefore, the EIS test provides an alternate and less intrusive method to track cell degradation. However, the EIS test does not provide any information on available energy. Since all INEEL ATD Gen 2 EIS testing is performed at 60% SOC, additional studies will be required to determine theSOC-dependence of this model.EIS Magnitude Growth (%)Figure 7. EIS magnitude growth as a function of test time0-7803-7467-3/02/$17.00 ?2002 IEEE.1854VII. ACRONYMS AND ABBREVIATIONSThe following acronyms and abbreviations were used in this paper: ATD BOL DOD DOE EOT FreedomCAR L-HPPC OCV PNGVAdvanced Technology Development beginning of life depth of discharge Department of Energy end of testFreedom Cooperative Automotive Research low-current hybrid pulse power characterization open circuit voltagePartnership for a New Generation of VehiclesRPT SOCreference performance test state of chargeBSF battery size factorACKNOWLEDGMENTThis work was prepared as an account of work sponsored by an agency of the United States Government under US DOE ContractDE-AC07-99ID13727. Funding for this work was provided by the U.S. DOE Office of Advanced Automotive Technologies.REFERENCES*1+ R.A. Sutula et al., “FY 2000 progress report for the Advanced Technology Development program,” U.S. DOE, OAAT, December 2000. *2+ Gary Henriksen, “Gen 2 Baseline & Variant C cells,” ATDQuarterlyReview Presentation in Albuquerque, N.M., November, 2000.[3] PNGV test plan for Advanced Technology Development Gen 2 lithium-ion cells, EVH-TP-121, Revision 6, October 2001.[4] PNGV battery test manual, DOE/ID-10597, Revision 3, February 2001. *5+ D. Zhang at al., “Studies on capacity fade of lithium-ion batteries,”Journal of Power Sources, vol. 91, pp. 122-129, 2000.EIS electrochemical impedance spectroscopy0-7803-7467-3/02/$17.00 ?2002 IEEE.1855。

磷酸锰铁锂文献

磷酸锰铁锂文献

磷酸锰铁锂文献磷酸锰铁锂是一种重要的锂离子电池正极材料,具有高比容量、良好的循环稳定性和较高的工作电压。

以下是一些相关的文献:1. An Optimized Electrode Slurry for High-Energy Li-Ion Cells Based on LiNi0.5Mn1.5O4 and a Mn-RichLi1.2Ni0.22Mn0.54Co0.24O2 Cathode: Electrochemical, Electrical Characterization and Safety Aspects. Journal of The Electrochemical Society, 2020. 167 (11): 110559.2. Synthesis and properties of LiFe0.94Mn0.06PO4/C composite cathode materials for lithium-ion batteries. Journal of Power Sources, 2016. 301: 101-105.3. Electrochemical per formance of LiFe1−yMgyPO4/C for Li-ion batteries. Journal of Solid State Electrochemistry, 2012. 16: 2599-2604.4. Ionothermal Synthesis of LiFePO4 and LiFe0.97Mn0.03PO4 Electrodes. Journal of The Electrochemical Society, 2007. 154 (9): A849-A852.5. Synthesis and characterizations of LiMn2-xFex(PO4)3/C cathode materials for lithium ion batteries. Electrochimica Acta, 2011. 56: 193-199.这些文献提供了关于磷酸锰铁锂的合成方法、结构特性、电化学性能以及应用方面的研究成果。

已定型的含阿拉伯数字的词语

已定型的含阿拉伯数字的词语

114青岛大学学报(工程技术版)第33卷[14]C h e n S C, W a n C C,W a n g Y Y. T h e r m a l Analysis of L i t h i u m-I o n Batteries[J]. Journal of P o w e r Sources, 2005,140(1):111-124.[15]李聪聪,陈强,喻凡,等.起停系统电池温度建模及试验研究)].汽车工程,2013,35(1):60 - 65.[16]胡明辉,秦大同,石万凯,等.混合动力汽车镍氢电池组温度场研究)].汽车工程,2007,29(1):37 -40.[17]杨世铭,陶文铨.传热学[M].4版.北京:高等教育出版社,2006.[18]段瑶娟.动力锂离子电池包热场分析与散热优化研究[D].北京:北京交通大学,2015.[19]余志生.汽车理论[M].5版.北京:机械工业出版社,2009.)0]喻凡,林逸.汽车系统动力学[M].北京:机械工业出版社,2005.Study on Temperature Characteristics of High-PowerLi-Ion Cells under NEDCL I Y u a n y u a n,H U O W e i,L I Z h i m i n g,F A N H u a m i n,H U A N G F u c h u a n g (School of Electrom echanic E n gin eerin g,Qingdao U n iv rrs ity,Qingdao 266071, C hina)Abstract:In this p a p rr, 18650-Li-ionbatteries are research ed,to explore the therm al characteristics of the high-power Li-ionbattery undrr the N E D C.A ccording to O C V curve of Li-ion battery and theJoule's law of internalre sista n t,the m athem atical model of heating characteristics of high-pow er Li-ionbattery based on N E D C is tablish ed.Based on Newton's cooling form ula and Stephen-Boltzm ann's la w,a m athem atical model of heat d isii-pation during battery N E D C operation is established.T hen therm al sim ulation of the battery is perform ed w ith-M atlab.T h e experim ental m ethod of therm al characteristics of high-pow er Li-ionbattery based on N E D C is ex­p lo red,and the circuit platform of the experim entis b uilt.T h e output power of the high-pow er Li-ioncell iscontrolled by the duty cycle of PW M w ave based on N E D C.D uring Experim ental p ro c ess,the experim ental da­ta im port into the hard disk of a P C that connected w ith an o scilloscop e,the device m easures experim ental vari­ables.T h e results show that the PW M w ave m ethod w hich is equivalent to N E D C output power cou m ission of m easurem ent during lithium b attery discharge in a high-pow er and the end of the second cy c le,the-high-pow er Li-ioncell is a bout to e x h a u st,and its internal resistance rose sh arp ly.T akin g into account the safe­ty problem at this tim e thehigh-pow er Li-ioncell should no longer be used.Keywords:N E D C#tem p eratu re#M a tla b#lithium-ion c e ll#single-chip摘要的写作要求摘要应按照四要素编写,即:目的(本人针对什么问题,或为解决什么问题)、方法(解决该问题采用 了那些方法,包括:所用的原理、理论、条件、对象、材料、工艺、结构、手段、装备、程序等)、结果(应陈述主要研究成果,包括所获得的实验结果。

YiyingWu(吴屹影):以武(吴屹影)

YiyingWu(吴屹影):以武(吴屹影)

Yiying Wu (吴屹影)The Ohio State University Phone: (614) 247-7810 Department of Chemistry Fax: (614)-292-1685 100 W 18th Avenue E-mail:***********************.edu Columbus, OH 43210EDUCATION:Dec. 2002 Ph.D. in Chemistry, University of California at Berkeley.Advisor: Prof. Peidong Yang.June. 1998 B.S. in chemical physics, University of Science and Technology of China.EMPLOYMENT:2005-present Assistant Professor, Chemistry Department, The Ohio StateUniversity. Interest: nanostructured functional materials.2003-2005 Postdoctoral Researcher, University of California at Santa Barbara, Department of Chemistry and Biochemistry, Advisor: Prof. Galen D.Stucky.HONORS:2010 NSF-CAREER Award2008 Cottrell Scholar Award, Research Corporation2001 MRS Graduate Student Silver Award, Boston.2001-2002Cal@Silicon Valley Fellowship, University of California at Berkeley. PROFESSIONAL MEMBERSHIPS:2001 American Chemical Society2001 Materials Research SocietyPUBLICATION LIST:u=undergraduate, g=graduate student, p=postdoc, s=senior personnel, *=corresponding author45. Y. Li g, G. Natu g, Y. Wu*. “LiFePO4/Graphene Composite as the CathodeMaterial for High-Power Lithium Ion Batteries” submitted to Nano Letters(2010).44. P. Hasin g, M. A. Alpuche-Aviles p, Y. Wu*.“Electrocatalytic activity ofgraphene multilayers towards I-/I3-: effect of preparation conditions andpolyelectrolyte modification” submitted to J. Physical Chemistry C (2010).43. G. Natu g, Y. Wu*. “Photoelectrochemical Study of the Ilmenite Polymorph ofCdSnO3 and its Photoanodic Application in Dye-Sensitized Solar Cells” J.Physical Chemistry C, accepted (2010).42. Y. Li g, P. Hasin g, Y. Wu*. “Ni x Co3-x O4 Nanowire Arrays for ElectrocatalyticOxygen Evolution”, Advanced Materials, accepted (2010).41. J. Baxter s, G. Chen s, D. Daniielson s, M. S. Dresselhaus s*, A. G. Fedorov s*, T. S.Fisher s, C. W. Jones s, E. Maginn s, U. Kortshagen s, A. Manthiram s, A. Nozik s, D.Rolison s, T. Sands s, L. Shi s*, D. Sholl s, Y. Wu s. “Nanoscale Design to Enablethe Revolution in Renewable Energy”, Energy & Environmental Science. 2(6), 559 (2009)40. Y. Li g, Y. Wu*. “Coassembly of Graphene Oxide and Nanowires for Large-Area Nanowire Alignment”, J. Am. Chem. Soc.131(16) 5851-5857 (2009).39. M. A. Alpuche-Aviles p, Y. Wu*. “Photoelectrochemical Study of the Bandstructure of Zn2SnO4Prepared by the Hydrothermal method”, J. Am. Chem.Soc.131(9) 3216-3224 (2009).38. P. Hasin g, M. A. Alpuche-Aviles p, Y. Li g, Y. Wu*. “Mesoporous Nb-dopedTiO2 as Pt Support for Counter Electrode in Dye-Sensitized Solar Cells”, J.Phys. Chem. C. 113(17) 7456-7460 (2009).37. Y. Li g, Y. Wu*. “Formation of Na0.44MnO2 nanowires via stress-inducedsplitting of birnessite nanosheets”,Nano Research, 2(1): 54-60 (2009). 36. Y. Li g, B. Tan p, Y. Wu*. "Mesoporous Co3O4 Nanowire Arrays for LithiumIon Batteries with High Capacity and Rate Capacity", Nano Letters, 8:265-270 (2008).35. Y. Li g, B. Tan p, Y. Wu*. "Ammonia-Evaporation-Induced Synthetic Methodfor Metal (Cu, Zn, Cd, Ni) Hydroxide/Oxide Nanostructures", Chem.Mater.20: 567-576 (2008).34. B. Tan p, E. Toman u, Y. Li g, Y. Wu*, "Zinc Stannate (Zn2SnO4) Dye-SensitizedSolar Cells", J. Am. Chem. Soc. 129(14), 4162 (2007).33. Y. Li g, B. Tan p, Y. Wu*, "Freestanding mesoporous quasi-single-crystallineCo3O4 nanowire arrays", J. Am. Chem. Soc. 128(44), 14258-14259 (2006)(highlighted by Nature Nanotech. (Oct. 2006)).32. B. Tan p, Y. Wu*, “Dye-Sensitized Solar Cells Based on Anatase TiO2Nanoparticle/Nanowire Composites”, J. Phys. Chem. B110: 15932-15938(2006).(Postdoc work)31. A. Thomas, M. Schierhorn, Y. Wu, G. Stucky, “Assembly of SphericalMicelles in 2D Physical Confinements and Their Replication intoMesoporous Silica Nanorods”, J. Mater. Chem. 17: 4558-4562 (2007). 30. M. Moskovits, D.H. Jeong, T. Livneh, Y.Y. Wu, G.D. Stucky, "Engineeringnanostructures for single-molecule surface-enhanced Raman spectroscopy", Isreal Journal. of Chemistry, 46: 283-291 (2006).29. Y. Zhang , J. Christofferson, A. Shakouri, D. Li, A. Majumdar, Y. Wu, R. Fan,P. Yang, “Characterization of heat transfer along Si Nanowire”, IEEETransactions on Nanotechnology, 5, 67 (2006).28.J. F. Wang, C.-K. Tsung, R. C. Hayward, Y. Wu, G. D. Stuck. “Single-crystal mesoporous silica ribbons”, Angew. Chem. Int. Ed.44: 332-336 (2005).27.Y. Wu, G. S. Cheng, K. Katsov, S. W. Sides, J. F. Wang, J. Tang, G. H.Fredrickson, M. Moskovits, G. D. Stucky, “Composite mesostructures bynano-confinement”, Nature Materials3, 816-822 (2004). (Highlighted byScience306, 943 (2004)).26.Y. Wu, T. Livneh, Y. X. Zhang, G. S. Cheng, J. F. Wang, J. Tang, M.Moskovits, G. D. Stucky, “Templat ed synthesis of highly orderedmesostructured nanowires and nanowire array”, Nano Letters 4, 2337(2004) (cover story).25.J. F. Wang, C.-K. Tsung, W. B. Hong, Y. Wu, J. Tang, G. D. Stucky,"Synthesis of mesoporous silica nanofibers with controlled porearchitectures", Chem. Mater. 16, 5169 (2004).24.J. Tang, Y. Wu, E. W. McFarland, G. D. Stucky, “Synthesis andphotocatalytic properties of highly crystalline and ordered mesoporousTiO2 thin films”, Chem. Comm. (14), 1670-1671 (2004).(Graduate work)23.A. R. Abramson, W. C. Kim, S. T. Huxtable, H. Q. Yan, Y. Wu, A. Majumdar,C.-K. Tien, P.D. Yang, "Fabrication and characterization of ananowire/polymer-based nanocomposite for a prototype thermoelectricdevice", Journal of Microelectromechanical Systems, 13(3), 505 (2004).).22.D. Y. Li, Y. Wu, R. Fan, P. D. Yang, A. Majumdar, “Thermal conductivity ofSi/SiGe longitudinal heterostructure nanowires” Appl. Phys. Lett. 83(15),3186 (2003).21.D. Y. Li, Y. Wu, P. Kim, L. Shi, N. Mingo, Y. Liu, P. D. Yang, A. Majumdar,“Thermal conductivity of individual silicon nanowires” Appl Phys. Lett.83(14), 2934 (2003).20.R. Fan, Y. Wu, D. Y. Li, M. Yue, A. Majundar, P. D. Yang, “Fabrication ofSilica Nanotube Arrays from Vertical Silicon Nanowire Templates”, J. Am.Chem. Soc.125(18), 5254-5255 (2003).19.Y. N. Xia, P. D. Yang, Y. Sun, Y. Wu, B. Mayers, B. Gates, Y. D. Yin, F. Kim,H. Yan, “One-dimensional Nanostructures: Synthesis, Characterization, andApplications”, Adv. Mater. 15(5), 353-389 (2003).18.Y. Wu, R. Fan, P. D. Yang, "Block-by-block growth of single-crystallineSi/SiGe superlattice nanowires", Nano letters, 2, 83 (2002).17.Y. Wu, H. Yan, M. Huang, B. Messer, J. Song, P. D. Yang, “Inoragnicsemiconductor nanowires: rational growth, assemblies and novel properties”, Chemistry, Euro. J., 8, 1260 (2002).16.Y. Wu, H. Yan, P. D. Yang, "Semiconductor nanowire array: potentialsubstrates for photocatalysis and photovoltaics", Topics in Catalysis, 19(2), 197 (2002).15.B. Gates, B. Mayers, Y. Wu, Y. Sun, B. Cattle, P. D. Yang, Y. N. Xia,“Synthesis and characterization of crystalline Ag2Se nanowires through atemplate-engaged reaction at room temperature”, Adv. Func. Mater. 12(10), 679-686 (2002).14.P. D. Yang, Y. Wu, R. Fan, “Inorganic semiconductor nanowires”,International Journal of Nanoscience,1(1), 1-39 (2002).13.B. Zheng, Y. Wu, P. D. Yang, J. Liu, “Synthesis of ultra-long and highly-oriented silicon oxide nanowires from alloy liquid”, Adv. Mater. 14, 122(2002).12.Y. Wu, P. D. Yang, “Direct observation of vapor-liquid-solid nanowiregrowth”, J. Am. Chem. Soc. 123, 3165 (2001).11.Y. Wu, B. Messer, P. D. Yang, "Superconducting MgB2 nanowires", Adv.Mater.13, 1487 (2001).10.Y. Wu, P. D. Yang, “Melting and welding semiconductor nanowires innanotubes”, Adv. Mater. 13, 520 (2001).9.M. Huang, S. Mao, H. Feick, H. Yan, Y. Wu, H. Kind, E. Weber, R. Russo, P.D. Yang, "Room-temperature ultraviolet nanowire nanolasers", Science,292, 1897 (2001).8.M. Huang, Y. Wu, H. Feick, N. Tran, E. Weber, P. D. Yang, “Catalytic growthof zinc oxide nanowi res through vapor transport”, Adv. Mater. 13(2), 113(2001).7.J. Song, Y. Wu, B. Messer, H. Kind, P. D. Yang, "Metal nanowire formationusing Mo3Se3- as reducing and sacrificing templates", J. Am. Chem. Soc.123, 10397 (2001).6. B. Gates, Y. Wu, Y. Yin, P. D. Yang, Y. D. Xia, “Single-crystalline nanowiresof Ag2Se can be synthesized by templating against nanowires of trigonalSe”, J. Am. Chem. Soc. 123, 11500 (2001).5.J. Song, B. Messer, Y. Wu, H. Kind P. D. Yang, "MMo3Se3 (M=Li+, Na+, Rb+,Cs+, NMe4+) nanowire formation via cation exchange in organic solution",J. Am. Chem. Soc. 123, 9714 (2001).4.Y. Li, J. Wang, Z. Deng, Y. Wu, X. Sun, S. Fan, D. Yu, P. D. Yang, “Bismuthnanotubes: a rational low-temperature synthetic route”, J. Am. Chem. Soc.123, 9904 (2001).3.Y. Wu, P. D. Yang, “Germanium/carbon core-sheath nanostructures”, Appl.Phys. Lett. 77, 43 (2000).2.Y. Wu, P. D. Yang, “Germanium nanowire growth via simple vapor transport”,Chem. Mater. 12, 605 (2000).1. B. Messer, J. H. Song, M. Huang, Y. Wu, F. Ki m, P. Yang, “Surfactantinduced mesoscopic assemblies of inorganic molecular chains”, Adv.Mater. 12, 1526 (2000).GRANTS and AW ARDS:9/07-8/10 Department of Energy, “Designing nanoparticle/nanowire composites and "nanotree" arrays as electrodes for efficient dye-sensitized solarcells”, $750,000 total9/06-9/08 Petroleum Research Fund PRF-43833, “Functional nanocrystal-nanowire composite materials: synthesis and electron transportproperties”, $35,000 total.7/08- Research Co rporation (Cottrell Scholar Award), “Searching for New Electrode Materials and Nanostructured Architectures for EfficientDye-Sensitized Solar Cells”; $100,000 total.2/10-2/15 NSF-CAREER, “Black Cobalt Oxide Nanowire Arrays: Synthesis, Properties, and Ene rgy Applications”; $575,000 totalINVITED PRESENTATIONS:Conferences/Workshops/Symposia16. FACCS conference, Lousville, KY, October 19, 2009.15. IMR Materials Week, Ohio State Unversity, August 31 – September 3, 2009.14. North American Solid State Conference, Ohio State University, June 17-20,2009.13. Central Regional Meeting of the American Chemical Society, Cleveland, May20-23, 2009.12. Materials Research Society meeting, San Francisco, April 13-17, 2009.11. Indo-US Workshop on nanoscale materials and interfaces, Purdue University,10-12 March 2009.10. Nanoparticles in Energy Applications Workshop, Argonne National Lab, Feb.23, 2009.9. ASME Heat transfer, Fluids, Energy Sustainability and Nanotechnology,Jacksonville, FL, Aug. 12, 20088. Central Regional Meeting of American Chemical Society, Columbus, OH,June 13, 20087. 35th Annual Spring Symposium, Michigan Chapter of the American VacuumSociety, Toledo, Oh, May 28, 20086. Wright Center PVIC Semi Annual meeting, Columbus, OH, April 17, 2008 5. 235th ACS National Meeting, New Orleans, LA, April 9, 20084. SPIE Optics East, Boston, MA, Sept. 9-12, 20073. Advanced Materials Workshop, Dalian, China, June 23-24, 20072. 223rd ACS national meeting, Chicago, IL, March 25-28, 20071. 41st ACS Midwest Regional Meeting, Quincy, IL, Oct. 25-27, 2006 Universities/Colleges13. IUPUI, Department of Mechanical Engineering, February 4, 2010.12. UC Davis, Department of Chemistry, January 5, 2010.11. University of Michigan, Department of Chemistry, October 30, 2009.10. Penn State University, Department of Chemistry &MRSEC, October 5, 2009.9. Purdue University, Department of Chemistry, September 16, 2009.8. The Ohio State University, ENCOMM, February 13, 20097. The Ohio State University, Department of Chemistry, January 14, 2009 (4th-year review).6. Indiana University, Department of Chemistry, April 22, 2008.5. Miami University, Department of Chemistry and Biochemistry, February 7,2008.4. Ohio University, Condensed matter and surface science seminar, May 17,2007.3. OSU, Department of Materials Science and Engineering, April 6, 2007.2. OSU, Department of Biomedical Engineering, February 2007.1. Kent State University, Department of Chemistry, September 22, 2005. PATENTS:4. “Graphene Compo sites as the Cathode Material of High-Power Lithium IonBatteries”, U.S. provisional patent, OSU1159-288A (2010).3. “Fluidic Nanotubes and Devices”, Patent No. US 7,355,216 B2 (April 8, 2008) 2. “Sacrificial Template Method of Fabricating a Nanotube”, Pa tent No.: US7,211,143 B2 (May 1, 2007).1. “Methods of fabricating nanostructures and nanowires and devices fabricatedtherefrom”, Patent N0.: WO02080280 (2002).LAB PERSONNEL:Present:Postdoctoral Associates:Dr. Dan Wang (May 2009-present)Graduate Students:Yanguang Li (5th year, Ph.D candidate); Panitat Hasin (3nd year); Gayatri Natu (3nd year); Ishika Sinha (3nd year); Tushar Kabre (2st year);。

磷酸铁锂电池火灾危险性分类

磷酸铁锂电池火灾危险性分类

磷酸铁锂电池火灾危险性分类董海斌, 张少禹, 李毅, 等. ncm811高比能锂离子电池热失控火灾特性[j]. 储能科学与技术, 2019, 8(s1): 65-70.[本文引用: 1]dong h b, zhang s y, li y, et al. thermal runaway fire characteristics of lithium ion batteries with high specific energy ncm811[j]. energy storage science and technology, 2019, 8(s1): 65-70.[本文引用: 1][2]forgez c, vinh d d, friedrich g, et al. thermal modeling of a cylindrical lifepo4/graphite lithium-ion battery[j]. journal of power sources, 2010, 195(9): 2961-2968.[3]huang p f, ping p, li k, et al. experimental and modeling analysis of thermal runaway propagation over the large format energy storage battery module withli4ti5o12 anode[j]. applied energy, 2016, 183: 659-673. [4]larsson f, mellander b e. abuse by external heating, overcharge and short circuiting of mercial lithium-ion battery cells[j]. journal of the electrochemical society, 2014, 161(10): a1611-a1617.[5]li d j, danilov d l, gao l, et al. degradation mechanisms of c6/lifepo4 batteries: experimental analyses of cycling-induced aging[j]. electrochimica acta, 2016, 210: 445-455.[本文引用: 1][6]feng x n, sun j, ouyang m g, et al. characterization of penetration induced thermal runaway propagation process within a large format lithium ion battery module[j]. journal of power sources, 2015, 275: 261-273.[本文引用: 1][7]lamb j, orendorff c j, steele l a m, et al. failure propagation in multi-cell lithium ion batteries[j]. journal of power sources, 2015, 283: 517-523.[8]lopez c f, jeevarajan j a, mukherjee p p. experimental analysis of thermal runaway and propagation inlithium-ion battery modules[j]. journal of the electrochemical society, 2015, 162(9): a1905-a1915.[9]li h, duan q l, zhao c p, et al. experimental investigation on the thermal runaway and its propagation in the large format battery module withli(ni1/3co1/3mn1/3)o2 as cathode[j]. journal of hazardous materials, 2019, 375: 241-254.[本文引用: 2][10]刘昱君, 段强领, 黎可, 等. 多种灭火剂扑救大容量锂离子电池火灾的实验研究[j]. 储能科学与技术, 2018, 7(6): 1105-1112.liu y j, duan q l, li k, et al. experimental study on fire extinguishing of large-capacity lithium-ion batteries by various fire extinguishing agents[j]. energy storage science and technology, 2018, 7(6): 1105-1112.[本文引用: 1][11]babrauskas v. pillow burning rates[j]. fire safety journal, 1985, 8(3): 199-200.[本文引用: 1][12]ribière p, grugeon s, morcrette m, et al. investigation on the fire-induced hazards of li-ion battery cells by fire calorimetry[j]. energy & environmental science, 2012, 5(1): 5271-5280.[本文引用: 2][13]ping p, wang q s, huang p f, et al. study of the fire behavior of high-energy lithium-ion batteries with full-scale burning test[j]. journal of power sources, 2015, 285: 80-89.[本文引用: 1][14]ping p, kong d p, zhang j q, et al. characterization of behaviour and hazards of fire and deflagration for high-energy li-ion cells by over-heating[j]. journal of power sources, 2018, 398: 55-66.[本文引用: 1][15]li h, chen h d, zhong g b, et al. experimental study on thermal runaway risk of 18650 lithium ion battery under side-heating condition[j]. journal of loss prevention in the process industries, 2019, 61: 122-129.[本文引用: 1][16]feng x n, sun j, ouyang m g, et al. characterization of large format lithium ion battery exposed to extremely high temperature[j]. journal of power sources, 2014, 272: 457-467.[本文引用: 1][17]larsson f, bertilsson s, furlani m, et al. gas explosions and thermal runaways during external heating abuse of mercial lithium-ion graphite-licoo2 cells at different levels of ageing[j]. journal of power sources, 2018, 373: 220-231.[本文引用: 1]1... 然而,由于自身的物理化学性质,当不正确使用时(热滥用、电滥用和机械滥用),磷酸铁锂电池会发生不可逆的热失控行为,存在较大的火灾危险性[1-5].在储能电站、变电站等实际运营场景中,往往将成百上千节的电池单体经过串并联后形成电池模组或者电池簇后集中使用.在该种情况下,一旦其中某节电池发生火灾,其释放的强热、燃烧等行为会造成周围电池温度上升,导致整个电池模组的热失控,甚至造成整个电池系统的火灾、爆炸事故[6-9].因此,在电化学储能以及变电系统等大规模应用场景中,研究锂离子电池热失控的火灾危险性并针对性开发相应的火灾抑制技术,对于电池系统的安全运行尤为重要. ...1... 然而,由于自身的物理化学性质,当不正确使用时(热滥用、电滥用和机械滥用),磷酸铁锂电池会发生不可逆的热失控行为,存在较大的火灾危险性[1-5].在储能电站、变电站等实际运营场景中,往往将成百上千节的电池单体经过串并联后形成电池模组或者电池簇后集中使用.在该种情况下,一旦其中某节电池发生火灾,其释放的强热、燃烧等行为会造成周围电池温度上升,导致整个电池模组的热失控,甚至造成整个电池系统的火灾、爆炸事故[6-9].因此,在电化学储能以及变电系统等大规模应用场景中,研究锂离子电池热失控的火灾危险性并针对性开发相应的火灾抑制技术,对于电池系统的安全运行尤为重要. ...1... 然而,由于自身的物理化学性质,当不正确使用时(热滥用、电滥用和机械滥用),磷酸铁锂电池会发生不可逆的热失控行为,存在较大的火灾危险性[1-5].在储能电站、变电站等实际运营场景中,往往将成百上千节的电池单体经过串并联后形成电池模组或者电池簇后集中使用.在该种情况下,一旦其中某节电池发生火灾,其释放的强热、燃烧等行为会造成周围电池温度上升,导致整个电池模组的热失控,甚至造成整个电池系统的火灾、爆炸事故[6-9].因此,在电化学储能以及变电系统等大规模应用场景中,研究锂离子电池热失控的火灾危险性并针对性开发相应的火灾抑制技术,对于电池系统的安全运行尤为重要. ...1... 然而,由于自身的物理化学性质,当不正确使用时(热滥用、电滥用和机械滥用),磷酸铁锂电池会发生不可逆的热失控行为,存在较大的火灾危险性[1-5].在储能电站、变电站等实际运营场景中,往往将成百上千节的电池单体经过串并联后形成电池模组或者电池簇后集中使用.在该种情况下,一旦其中某节电池发生火灾,其释放的强热、燃烧等行为会造成周围电池温度上升,导致整个电池模组的热失控,甚至造成整个电池系统的火灾、爆炸事故[6-9].因此,在电化学储能以及变电系统等大规模应用场景中,研究锂离子电池热失控的火灾危险性并针对性开发相应的火灾抑制技术,对于电池系统的安全运行尤为重要. ...2... 然而,由于自身的物理化学性质,当不正确使用时(热滥用、电滥用和机械滥用),磷酸铁锂电池会发生不可逆的热失控行为,存在较大的火灾危险性[1-5].在储能电站、变电站等实际运营场景中,往往将成百上千节的电池单体经过串并联后形成电池模组或者电池簇后集中使用.在该种情况下,一旦其中某节电池发生火灾,其释放的强热、燃烧等行为会造成周围电池温度上升,导致整个电池模组的热失控,甚至造成整个电池系统的火灾、爆炸事故[6-9].因此,在电化学储能以及变电系统等大规模应用场景中,研究锂离子电池热失控的火灾危险性并针对性开发相应的火灾抑制技术,对于电池系统的安全运行尤为重要. ...... 随着温度持续升高,电池内部热反应持续加快,100%与50% soc锂离子电池分别在2253 s和2611 s形成二次射流火,而对于0% soc的锂离子电池,因为电池内部能量较低,电池内部化学反应过程相对缓慢[9, 15],其燃烧行为明显缓和,在整个过程中并未出现多次射流火现象. ...1... 本文以228 a·h的磷酸铁锂为研究对象,通过自主搭建的锂离子电池火灾燃烧实验平台研究了目标电池的火灾危险性[10],并进一步分析了荷电状态对其火灾行为的影响规律,为锂离子电池的安全设计及火灾防控提供理论和技术支撑. ...1... 热释放速率是进行火灾危险性研究、分析样品火灾危险性的重要参数[11-13].其计算方式主要依据氧消耗原理,即通过精确测量燃烧过程中体系中的氧消耗量进而计算得到该过程的热释放速率[14],如式(1)所示. ...2... 如图7所示,相比于100% soc锂离子电池的剧烈燃烧,50%与0% soc锂离子电池的燃烧行为较为缓和.在本次实验中,50% soc锂离子电池的热释放速率曲线存在3个明显的峰值,这与实验观察到的射流火次数相符.但是由于电池内部热反应过程较为缓慢,持续时间较长,因此其最高峰值出现在第1个峰值,为52.82 kw,约为100% soc电池峰值的53.4%.而对于0% soc的锂离子电池,在经历初次射流火后即进入持续的稳定燃烧阶段,直至最终火焰熄灭,因此整个实验过程中仅观察到一个明显的hrr峰值,为41.74 kw.对应50%与0% soc 锂离子电池的总燃烧热(10.33 mj、7.68 mj)分别为100% soc(13.94 mj)电池的74.1%和55.1%.可以看出,随着soc的降低,电池燃烧剧烈程度明显降低,对应热释放速率峰值以及总燃烧热随之降低.而电池的总燃烧热不仅与电池的燃烧剧烈程度相关,还与燃烧的持续时间相关,因此soc对电池燃烧释放总燃烧热的影响并不明显,这一特性也被其他研究者所证实,如ribiere等[12]以2.9 a·h的软包limn2o4/石墨电池为研究对象,实验研究了不同荷电状态锂离子电池的燃烧产热,研究发现50% soc的电池燃烧总热量为383 kj,高于100% soc电池的313 kj.造成该现象的原因是soc较低的锂离子电池的发生热失控对应反应物的消耗速率较低,进而延长了电池的燃烧时间. ...... 为了更好地了解锂离子电池的火灾危险性,图8比较了不同soc锂离子电池与几种常见燃料的热释放速率[12].100% soc 样品电池的标准化热释放速率峰约为2.91 mw/m2,超过汽油的标准热释放速率峰(2.2 mw/m2),50% soc与0% soc锂离子电池燃烧时的热释放速率峰分别为1.55 mw/m2与1.22 mw/m2,介于汽油(2.2 mw/m2)与燃油(1.1 mw/m2)之间. ...1... 热释放速率是进行火灾危险性研究、分析样品火灾危险性的重要参数[11-13].其计算方式主要依据氧消耗原理,即通过精确测量燃烧过程中体系中的氧消耗量进而计算得到该过程的热释放速率[14],如式(1)所示. ...1... 热释放速率是进行火灾危险性研究、分析样品火灾危险性的重要参数[11-13].其计算方式主要依据氧消耗原理,即通过精确测量燃烧过程中体系中的氧消耗量进而计算得到该过程的热释放速率[14],如式(1)所示. ...1... 随着温度持续升高,电池内部热反应持续加快,100%与50% soc锂离子电池分别在2253 s和2611 s形成二次射流火,而对于0% soc的锂离子电池,因为电池内部能量较低,电池内部化学反应过程相对缓慢[9, 15],其燃烧行为明显缓和,在整个过程中并未出现多次射流火现象. ...1... 图4(d)给出了电池的电压变化趋势,在本次实验中发现,电池的电压跳水时间较晚于其安全阀破裂时间,这是由于造成电压掉落的主要原因是隔膜收缩熔融,而隔膜的收缩温度通常在130 ℃以上[16].而电池的sei膜在90 ℃时即发生分解,造成负极活性材料与电解液反应并产生一定量的气体,造成电池内部压力持续升高[17].而在电压跳水之前,随着温度的升高,电池电压表现出微量的衰减,这是由于电池的正、负极材料溶解所致.因此,在实际应用过程中,可考虑采用气体信号和电、热信号相结合的手段,对磷酸铁锂电池的热失控行为进行预测预警. ...1... 图4(d)给出了电池的电压变化趋势,在本次实验中发现,电池的电压跳水时间较晚于其安全阀破裂时间,这是由于造成电压掉落的主要原因是隔膜收缩熔融,而隔膜的收缩温度通常在130 ℃以上[16].而电池的sei膜在90 ℃时即发生分解,造成负极活性材料与电解液反应并产生一定量的气体,造成电池内部压力持续升高[17].而在电压跳水之前,随着温度的升高,电池电压表现出微量的衰减,这是由于电池的正、负极材料溶解所致.因此,在实际应用过程中,可考虑采用气体信号和电、热信号相结合的手段,对磷酸铁锂电池的热失控行为进行预测预警. ...。

一种由电子级碳酸锂制备电子级氟化锂的方法

一种由电子级碳酸锂制备电子级氟化锂的方法

一种由电子级碳酸锂制备电子级氟化锂的方法摘要:本研究旨在探索一种用于制备电子级氟化锂的电子级碳酸锂制备方法。

我们通过对碳酸锂原料的精细加工和纯化过程进行了一系列优化,以获得高纯度的电子级碳酸锂。

随后,我们将所得的电子级碳酸锂与氢氟酸反应,并通过后续的热处理步骤来制备电子级氟化锂。

实验结果表明,经过我们优化的制备方法得到的电子级氟化锂具有优良的纯度和晶体结构,满足了电子工业对高纯度氟化锂的要求。

该方法具有简单、高效和可扩展性的特点,可为电子级氟化锂的制备提供一种可行的途径。

关键词:电子级碳酸锂,电子级氟化锂,纯化,制备方法,高纯度前言:电子级氟化锂作为一种重要的材料,在电子器件、电池等领域具有广泛的应用。

其高纯度和优良的晶体结构对于电子工业的发展至关重要。

目前,制备电子级氟化锂的方法包括氢氟酸法[1-3]、溴化锂法[4-5]等,但这些方法存在一些问题,如生产工艺复杂、废物处理困难等。

为了满足电子工业对高纯度氟化锂的需求,研究人员一直致力于寻找一种简单、高效且可扩展的制备方法。

因此,本研究旨在探索一种新的制备电子级氟化锂的方法,通过优化反应条件和纯化步骤,提高氟化锂的纯度和晶体结构,并评估其在电子工业中的应用潜力。

在本文中,我们首先对商业碳酸锂原料进行精细加工和纯化处理,以去除杂质,获得高纯度的电子级碳酸锂。

随后,我们采用一种有效的方法进行氟化反应,将碳酸锂转化为氟化锂。

在氟化反应后,通过多次纯化步骤,我们进一步净化氟化锂,以去除残留的杂质。

最终,我们通过浓缩和结晶等方法获得了高纯度的电子级氟化锂晶体。

通过对所得到的电子级氟化锂样品进行表征和测试,我们将评估其纯度、晶体结构和电化学性能。

这些结果将为电子器件中的锂离子电池等应用提供高质量的原材料,并促进电子工业的发展。

本研究的成果将有助于提供一种简单、高效且可扩展的制备方法,为满足电子工业对高纯度氟化锂的需求提供新的解决方案。

这将为电子器件的性能提升和新技术的发展奠定基础,推动电子工业向更高水平迈进。

单离子导体聚合物电解质及其电池应用

单离子导体聚合物电解质及其电池应用

单离子导体聚合物电解质及其电池应用摘要:本文综述了单离子导体聚合物固态电解质的性能特点和研发进展,主要内容包括聚合物固态电解质的特点、单离子导体聚合物电解质的优劣势与材料性能要求,以及不同单离子导体聚合物电解质材料的性质、对应的固态电池应用与研发进展,并分析了单离子导体聚合物固态电解质的未来研发趋势,并阐述其在新能源领域未来规模化应用的发展愿景。

关键词:单离子导体;聚合物固态电解质;锂电池中图分类号:TM9120引言固态电池用固态电解质替代闪点低易燃易爆且易泄露的电解液,能极大改善锂电池的安全问题。

聚合物固态电解质具备结构可调、离子电导率大、与电极界面相容性佳、质轻柔韧等优点,但存在极化和副反应等问题,阻碍了其大规模商用。

采用单离子导体聚合物电解质,是一个极佳解决方案。

1 单离子导体聚合物电解质1.1聚合物电解质的特点与问题聚合物固态电解质,具有较好的柔韧性和界面润湿性,能与电极保持良好界面接触,赋予固态电池充放电循环稳定性。

目前聚合物电解质大多是双离子聚合物电解质,存在极化和副反应等问题,双离子电解质电导率是由阴阳离子共同组成的,高电导率并不一定意味着锂离子迁移效率高,实际上锂离子的迁移才是真正的有效电荷转移。

1.2 单离子导体聚合物电解质的优劣势与性能要求过多的阴离子聚集在正极表面,在正负极之间产生了一个浓度梯度,这会使得电池内部产生一个浓差极化,导致较大的过电势,限制了锂离子电池能量密度和功率密度的提升。

因此,在高的电导率下,若能保持高的迁移系数,对提升锂离子电池的能量密度意义重大。

单离子导体聚合物电解质,将阴离子通过化学共价键固定在聚合物分子主链骨架,是一种极佳的固态电解质。

与传统的双离子聚合物电解质相比,单离子导体聚合物电解质具有更高的离子迁移数和良好的电化学稳定性,面临的主要问题是其锂离子电导率较低、合成难度大。

为改善单离子导体聚合物电解质的锂离子电导率,对聚合物的结构设计提出了更多要求,设计合成出具有优异性能的单离子导体聚合物电解质,对于改善固态电池性能极为重要。

一种双氟磺酰亚胺锂的制备方法

一种双氟磺酰亚胺锂的制备方法

一种双氟磺酰亚胺锂的制备方法摘要:双氟磺酰亚胺锂是一种重要的化学品,具有广泛的应用前景。

本研究旨在开发一种简单、高效且可扩展的制备方法,并对其进行全面的表征。

我们选择商业氟磺酰亚胺和锂盐作为起始物,经过预处理和纯化,利用合成反应成功合成了双氟磺酰亚胺锂。

通过优化反应条件和纯化工艺,获得了高纯度的产物。

我们对样品进行了热稳定性、溶解性和电化学性能等方面的测试和评估。

实验结果表明,制备的双氟磺酰亚胺锂具有良好的热稳定性、溶解性和电化学性能,且能够溶解于常见的有机溶剂中。

这些特性为其在电池等领域的应用提供了坚实的基础。

本研究为制备高纯度的双氟磺酰亚胺锂提供了一种简单有效的方法,并为其进一步的应用研究提供了重要的参考依据。

关键词:双氟磺酰亚胺锂,制备,反应条件,表征,电化学分析前言:双氟磺酰亚胺锂是一种具有广泛应用前景的重要化学物质,用于电化学储能、催化剂和有机合成等领域。

为了实现其广泛应用,需要开发简单高效的制备方法。

目前已有溶剂法[1-2]、离子交换法[3-4和化学反应法[5]等方法可供选择,但存在一些问题。

因此,本研究旨在开发一种简单高效的制备方法,并对其进行全面表征。

通过优化反应条件和纯化工艺,我们将选择合适的起始物,探索制备高纯度双氟磺酰亚胺锂的最佳方法。

同时,对样品进行物性和电化学性能测试,验证其适用性和性能优势。

1.实验方法1.1原料和试剂准备本实验中使用的原料包括商业氟磺酰亚胺和锂盐。

商业氟磺酰亚胺作为起始物,具有较高的纯度,并且广泛应用于电化学和有机合成领域。

锂盐作为反应的锂源,常见的有氟化锂和硫酸锂。

1.2制备步骤实验中采用合成反应法制备双氟磺酰亚胺锂。

具体步骤如下:1.2.1预处理商业氟磺酰亚胺和锂盐需要进行预处理,以去除其中的杂质和水分。

首先,商业氟磺酰亚胺通过真空干燥的方式去除其中的水分。

然后,锂盐在惰性气氛下加热,使其脱水,并去除其中的杂质。

1.2.2反应条件优化在合成反应中,我们优化了反应温度、摩尔比和反应时间等因素。

高镍三元电池热反应机理及其改善性研究进展

高镍三元电池热反应机理及其改善性研究进展

高镍三元电池热反应机理及其改善性研究进展张跃强;田君;赵鼎;高洪波;徐春常【摘要】高能量密度锂离子电池高镍三元电池使用过程中易发生热失控现象,存在不可忽视的安全隐患,其热失控主要是由正极材料及电解液的相关热反应造成的.综述了高能量密度锂离子电池正极材料和电解液的热反应机理的研究进展,并明确了当前研究中的不足之处.为探究改善高能量密度锂离子电池正极材料和电解液热稳定性的方法和有效解决高能量密度锂离子电池的安全问题指明了方向.【期刊名称】《电源技术》【年(卷),期】2019(043)007【总页数】4页(P1223-1225,1229)【关键词】高能量密度;锂离子电池;正极材料;电解液;热稳定性【作者】张跃强;田君;赵鼎;高洪波;徐春常【作者单位】中国北方车辆研究所,北京100072;北京电动车辆协同创新中心,北京100081;中国北方车辆研究所,北京100072;北京电动车辆协同创新中心,北京100081;中国北方车辆研究所,北京100072;中国北方车辆研究所,北京100072;北京电动车辆协同创新中心,北京100081;中国北方车辆研究所,北京100072;北京电动车辆协同创新中心,北京100081【正文语种】中文【中图分类】TM912.9为减少传统化石能源的消耗、改善人类生活环境,目前,欧美、日韩及中国在大力推行新能源汽车;近些年来,我国的纯电动汽车得到政策的大力支持和迅猛发展。

纯电动汽车的核心部件为动力电池,与铅酸、氢镍、镉镍等传统电池相比,锂离子电池具有能量密度高、工作电压高、无记忆效应、环境友好等优点(图1),目前电动汽车主要采用动力锂离子电池。

图1 锂离子电池与其他电池的性能对比[1]锂离子电池的组成部分主要有正极、负极、电解质、隔膜等。

正极材料提供了锂的来源,对锂离子电池的容量、电压、稳定性和成本等起到了主要作用[1-2]。

常见的商业化锂离子电池正极材料主要包括 LiFePO4、LiMn2O4、LiCoO2和三元材料LiNixCoyMzO2(M=Mn/Al)。

不和锂反应的有机溶剂

不和锂反应的有机溶剂

不和锂反应的有机溶剂不和锂反应的有机溶剂1. 引言在当今社会,锂离子电池作为一种重要的能量存储设备,应用广泛,如移动电子设备、电动车辆等。

然而,锂离子电池的安全性仍然是一个受到关注的问题。

当锂离子电池与某些有机溶剂发生反应时,可能导致电池过热、起火或爆炸等严重的安全事故。

寻找不和锂反应的有机溶剂对于提高锂离子电池的安全性至关重要。

2. 不和锂反应的有机溶剂的定义不和锂反应的有机溶剂是指在与锂金属或锂离子接触时,不会引起剧烈的反应,不会导致电池的过热、起火或爆炸等现象。

这种溶剂具有良好的热稳定性和化学性质,能够在锂离子电池中提供稳定的电解质性能。

3. 不和锂反应的有机溶剂的特点(1)热稳定性:不和锂反应的有机溶剂应具有良好的热稳定性,能够在锂离子电池的高温环境下保持稳定的性质,不发生分解或挥发。

(2)电解质溶解能力:不和锂反应的有机溶剂应能够溶解锂盐,保证锂离子在电池中的传导性能。

(3)低挥发性:不和锂反应的有机溶剂应具有较低的挥发性,减少溶剂的损失和电池的自放电。

(4)化学惰性:不和锂反应的有机溶剂在锂离子电池中不会与锂金属或锂离子发生剧烈的化学反应,确保电池的安全性。

4. 不和锂反应的有机溶剂的应用不和锂反应的有机溶剂广泛应用于锂离子电池的电解质系统中。

常见的不和锂反应的有机溶剂包括碳酸酯类、磷酸酯类、硅酮类、醚类、醇类等。

这些有机溶剂具有良好的热稳定性、电解质溶解能力和化学惰性,适用于不同类型的锂离子电池。

不和锂反应的有机溶剂在锂离子电池中起到了至关重要的作用。

它们不仅提供了电荷传输的介质,还能稳定电池的结构和性能。

通过寻找和开发更多不和锂反应的有机溶剂,可以进一步提高锂离子电池的安全性和性能。

5. 个人观点和理解在我看来,寻找不和锂反应的有机溶剂对于提高锂离子电池的安全性至关重要。

锂离子电池在现代社会发挥着重要的作用,但其安全性问题无法忽视。

通过使用不和锂反应的有机溶剂,可以有效降低电池发生过热、起火或爆炸等安全事故的风险。

不同原因引起的锂离子电池爆炸产物的初步分析及研究

不同原因引起的锂离子电池爆炸产物的初步分析及研究

不同原因引起的锂离子电池爆炸产物的初步分析及研究研发中心曹建华,毛焕宇1. 前言在锂离子电池商业化后的十多年中,应用在手机、笔记本电脑、数码相机等数码通讯产品上的锂离子电池爆炸事件层出不穷。

世界各国的锂电研究人员一直致力于解决锂电池爆炸的问题,并在爆炸机理上有过探讨[1-4],但在化学机理上的研究很少,以至于找不到对提高安全性很有效的方法。

本研究针对这一问题从锂离子电池爆炸产物分析入手,希望解释锂离子电池在不同状态下的爆炸过程,并有可能提出相应的安全解决办法。

2. 实验部分2.1 实验样品的基本情况本研究主要制作了053048A、423048A、103450AR以及18650等几种锂离子电池进行实验。

所涉及的锂离子电池是以LiCoO2为正极活性材料、石墨为负极活性材料的液态锂离子电池,此类锂电池目前占据着市场的主要地位,其主要原材料组成见表1。

表1. 实验用锂离子电池的主要原材料序号部件名称材料主要成份1 正极片 LiCoO2、铝箔、PVDF2 负极片石墨、铜箔、SBR、CMC3 电解液LiPF6+(EC+EMC+PC)4 隔膜纸 PE、PP5 极耳Ni6 壳体铝或钢7 胶纸 PET、PP、聚酰亚胺8 隔圈PP2.2 滥用实验为获得爆炸后的电池,我们安排了以下滥用模拟实验。

(1) 过充试验采用Newware充电柜,将充电至4.2V的电池搁置于一带有泄爆孔的盒子内,用3C 倍率的电流充电,直至电池爆炸,待冷却至室温后收集电池爆炸的固体残留物。

(2) 内短路试验用厚度为10mm的高容量电池进行该试验,制作电池时,在内部负极片极耳位置仅用一层PE隔膜与正极片隔离,并将负极耳的厚度减至0.07mm,宽度减至2mm。

将电池充电至4.2V,在正负极位置焊接线路电阻小于20mΩ的短路线,当合上开关发生外短路时,负极耳位置迅速发热,温度急剧上升导致靠近负极耳的隔膜融化,造成正负极片直接接触形成内短路,最终导致电池爆炸。

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Journal of Power Sources 196 (2011) 5349–5356Contents lists available at ScienceDirectJournal of PowerSourcesj 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 /j p o w s o urCharacterization of high-power lithium-ion batteries by electrochemical impedance spectroscopy.II:ModellingD.Andre a ,∗,M.Meiler a ,K.Steiner a ,H.Walz a ,T.Soczka-Guth a ,D.U.Sauer ba Deutsche ACCUmotive GmbH &Co.KG,Neue Str.95,D-73230Kirchheim/teck,GermanybRheinisch Westfälische Technische Hochschule Aachen,Jägerstr.17,D-52066Aachen,Germanya r t i c l e i n f o Article history:Received 15June 2010Received in revised form 16July 2010Accepted 25July 2010Available online 3 August 2010Keywords:Lithium-ion batteriesElectrochemical impedance spectroscopy Equivalent circuit modelsa b s t r a c tA common way to model lithium-ion batteries is to apply equivalent circuit (EC)models.In this work two different EC models are build up and parameterized for a commercial 6.5Ah high-power lithium-ion cell.Measured impedance spectroscopy data depending on temperature and state of charge (SOC)are used for parameter estimation.The first EC model consists of an ohmic resistor (R),an inductor (L)and three RC-elements (a parallel connection of a capacitor (C)and a resistor).The second EC model consists of one R,one L,two Zarc ele-ments and a Warburg element.The estimated parameters were used to develop two empirical electrical cell models which are able to predict the voltage of the cells depending on current,temperature and SOC.Hereby the internal cell resistance Ri is based on the EC models and a Butler–Volmer adjustment.Both approaches were validated by current profiles,which cover typical automotive applications to prove the model performance at low temperatures and high dynamic operation.An accurate voltage prediction could be realized with both EC models.The second,more complex,model is able to predict cell voltage more precisely,but at the expense of up to four times higher computational effort.© 2010 Elsevier B.V. All rights reserved.1.IntroductionIn order to predict the performance of a battery cell depending on operation conditions and load,simulations based on an equiv-alent circuit (EC)model are widely used [1,2].In this work two EC models with different complexities are presented and compared in terms of simulation performance and effort.The generalized method to identify these models is presented in Fig.1.In the first step the parameters of the model have to be esti-mated.Therefore impedance spectra gained by the EC are fitted to experimental measured data through a numerical optimization.Afterwards the estimated parameters are implemented into a cell model.Finally,the model is validated by comparison to measured data.A precise prediction of voltage allows testing battery cells under different conditions just by simulation and therefore reduces experimental efforts and time.Moreover simulations allow an opti-mization of the battery and in the next step of drive trains for upcoming hybrid and electrical vehicles.∗Corresponding author.Tel.:+49(0)7021892589;fax:+49(0)7113052142286.E-mail address:dave.andre@ (D.Andre).In a previous work [3]impedance spectra were recorded for a high-power 6.5Ah lithium-ion cell in a temperature range from −30◦C to 50◦C for the entire state of charge (SOC)range.These spectra contain all information about cell impedance depend-ing on operating conditions and allow therefore a prediction of the cell performance under different loads and scenarios.Based on these spectra both EC models are set,verified,validated and compared in terms of computation time and accuracy of voltage prediction.2.Theory2.1.Equivalent circuit with RC-elementsThe first applied EC to model cell voltage was built up in a most simple way in order to have a basic model.Aim of this approach is to gain a very fast computing model and to get a benchmark for an advanced EC model.The EC consists of one element for every section of the ideal impedance spectrum of lithium-ion cells and is displayed in Fig.2.The impedance behaviour of the cell at very high frequencies is represented by an ideal inductor L and the ohmic resistance by a resistor R .The following electrochemical processes at the elec-trodes can be represented in a most simple way by RC-elements,0378-7753/$–see front matter © 2010 Elsevier B.V. All rights reserved.doi:10.1016/j.jpowsour.2010.07.0715350 D.Andre et al./Journal of Power Sources196 (2011) 5349–5356Fig.1.Approach of system identification for an EC model.a parallel connection of a capacitor C and a resistor R .Thus the impedance of the system can be described as the sum of its ele-ments:Z RC =jωL +R 1+11/R 2+jωC 2+11/R 3+jωC 3+11/R 4+jωC 4.(1)This approach is a state of the art EC [4–7]and has in total eightparameters which have to be estimated and fitted by an optimiza-tion algorithm.2.2.Equivalent circuit with Zarc and Warburg elementThe goal of the second EC is a most accurately and meaningful reproduction of the measured impedance data.An approach with Zarc and Warburg elements suggested by several authors [8–10]is shown in Fig.3.2.2.1.The Zarc elementZarc elements are a parallel connection of a resistor R and a constant-phase-element (CPE)[11].CPEs consist of ageneralizedFig.2.Ideal impedance spectrum of a lithium-ion cell and an EC with three RC-elements.Fig.3.Ideal impedance spectrum of a lithium-ion cell and an EC with Zarc and Warburg element.capacity Âand depression factor and are defined by Z CPE =1(jω)Â.(2)A parallel connection with a resistor leads to Eq.(3):Z Zarc =11/R +(jω)Â.(3)Comparing Eq.(3)with the RC-element of Eq.(1)both equations are equal,if is left aside.This depression factor ,valid between zero and one,is respon-sible for the depression of the semi-circle in a Nyquist plot as Fig.4illustrates.For =0the Zarc element represents only an ohmic resistance and for =1the ideal semi-circle of a RC-element.The advantage of Zarc elements is their potential to reproduce the depression of semi-circles in impedance spectra,which are char-acteristic for lithium-ion cells.However,the disadvantage of Zarc elements is a missing Laplace transformation.Thus it is not possible to transfer the parameter sets from the frequency domain into the time domain without approximations [12].Buller [13]introduced in his thesis a way to approximate Zarc elements by a variable number of RC-elements as illustrated in Fig.5.The principle of this approximation is based on an odd num-ber of semi-circles whose radii are increasing towards the medium semi-circle.The resistance and capacity of each RC-element can be computed by optimization factors which are listed in the literature [13].In Fig.6,the result of an approximation with fiveRC-elements,Fig.4.Impact of depression factor on the Nyquist plot of the Zarc element (R =1m ,C =1kF).D.Andre et al./Journal of Power Sources196 (2011) 5349–53565351Fig.5.Approximation of the Zarc element withfiveRC-elements.Fig.6.Nyquist plot of a Zarc approximation withfive RC-elements,the dash-dotted line represents the ideal Zarc element,the dashed line represents the circuit with five RC-elements and the solid line represents the circuit with just one RC-element (R=10m ,C=2kF and=0.9).as used in this work,in comparison to an approximation with just one RC-element is shown.Especially for high values of the approximation matches the ideal curve very accurate and is therefore valid.2.2.2.The Warburg elementAnalogous to the Zarc element,an approximation is required for the Warburg element.A Warburg element is defined byZ w=R tanh(jωÂ)jωÂ(4)and shows a linear slope with an angle of45◦at high frequencies. This linear slope predestinates Warburg elements to represent the diffusion process of Fig.3.A simple way to approximate the Warburg element is a series connection of a resistor and a RC-element as illustrated in Fig.7. An approach applied by Handschuh[14].The impedance for this connection isZ w=R1+11/R22.(5)For the estimation of the parameters R1,R2and C2,the frequencyω0 where the spectrum reaches its minimum value is required.Hand-schuh[14]showed that the value ofω0is independent of R and can be approximated well byω0=2.53.(6)Furthermore it was shown that the minimum value of the spec-tra depends only on the resistanceZ min =−512R.(7)Fig.7.Nyquist plot of Warburg element,the solid line represents the ideal Warburgelement and the dashed line represents the R–RC circuit.By using this equation,the parameters can be determined:R1=16R,(8)R2=56R,(9)C2=1ω0R2=651ω0R.(10)In order to get an approximated slope of45◦,R1has to be separatedin additional two RC-elements with following parameters:R1,1=124R,(11)R1,2=324R,(12)C1,1=1100C2,(13)C1,2=13C2.(14)Finally,this approximation allows to representing the slope withhigh accuracy as demonstrated in Fig.8.Since for this work just the linear part of the Warburg elementis required,the last approximation is done for the intersection of atangent which runs through the point of origin and the RC-elementby their geometrical relation:R3=1−√0.52R2,(15)C3=22.42·(1−0.5)C2.(16)By using these approximations it is possible to represent the War-burg element accurately.Thus the impedance of the advanced EC5352 D.Andre et al./Journal of Power Sources196 (2011) 5349–5356Fig.8.Nyquist plot of a Warburg approximation with three RC-elements,the red line represents the ideal Warburg element and the blue line represents the 3-RC circuit.(For interpretation of the references to color in this figure legend,the reader is referred to the web version of the article.)can be computed by the equation corresponding to Fig.3:Z ZW =jωL +R 1+11/R 2+Â2·(jω) 1+11/R 3+Â3·(jω)2+Rtanh (jωÂ4)jωÂ4.(17)In total this EC has ten parameters,two parameters more than the first EC,increasing the computation time but also the accuracy of the simulation.3.Parameter estimation3.1.Equivalent circuit with RC-elementsIn this section,the parameters of the introduced ECs are esti-mated by numerical optimization.For this purpose a nonlinear curve-fitting optimization based on the method of least-squareswas used for every spectrum.For in total 119spectra,the parame-ters were estimated and interpolated to a characteristic map.Sincefor low temperatures no diffusion section was recorded by the electrochemical impedance spectroscopy (EIS)because of too low frequencies,an additional algorithm was required.This algorithm was able to detect the existence of a diffusion section in the mea-sured data and was setting R 3and C 3to zero if no diffusion process was recorded.The method of optimization is illustrated in Fig.9by plotting measured and fitted curves for an exemplary SOC of 60%at different temperatures in Nyquist plots.The general behaviour is similar for all temperatures.The simple EC is able to approximate the general behaviour of the curves,but fails to reproduce the spectra accu-rately.Problematic are the loops of the measured spectra which are depressed semi-circles and therefore difficult to fit by ideal ones and the almost linear diffusion part.Therefore large deviations can be seen especially in the middle of the first and second RC-element and for the linear slope at low frequencies.Since very high frequen-cies have no practical relevance for the simulation of batteries,the inductivity was neglected and is not represented.3.2.Equivalent circuit with Zarc and Warburg elementThe same optimization approach was applied to the second EC with Zarc and Warburg elements.The EC with estimated parame-ters was again compared to measured data and the result is given in Fig.10.It is obvious that this EC represents the measured data with a higher accuracy.Both,the semi-circles as well as the diffusion part are approximated very precisely by the Zarc and Warburg elements.Especially,the depressed semi-circles are represented very well by the depression factor .However,small variations can still be seen for elevated temperatures at thechange from the second Zarc element to the Warburg element.parison of measured and simulated EIS data by the EC with RC-elements for different temperatures at 60%SOC,the solid line represents the measured spectra and the dashed line represents the simulated spectra.D.Andre et al./Journal of Power Sources196 (2011) 5349–53565353parison of measured and simulated EIS data by the EC with Zarc and Warburg elements for different temperatures at60%SOC,the solid line represents the measured spectra and the dashed line represents the simulated spectra.4.ModellingThe estimated parameters were used to build cell models.Input parameters of this model were current I,cell capacity C,cell tem-perature T and initial state of charge SOC t=0.By integrating the cell current,the actual SOC could be determined continuously.Fur-thermore the open-circuit voltage(OCV)curve of the cell,which was shown in[1],was approximated as a function of SOC by a lookup table.By adding the overvoltagesÁof the system,which are provided in form of the EC parameters,the actual cell voltage was computed and visualized.4.1.Butler–Volmer adjustmentSince no DC-offset was used for the EIS measurements the effect of current on cell overvoltage was unknown.However,this effect is important for the charge transfer and is defined by the Butler–Volmer(BV)equation:i=i0·(e˛zF/RT(E−E eq)−e−((1−˛)zF/RT)(E−E eq))(18) where i is the electrode current density,i0is the exchange cur-rent density,˛is the symmetry factor,z is the number of electrons, E is the electrode potential,E eq is the equilibrium potential,F is the Faraday constant,R is the universal gas constant and T is the temperature.In order to consider the impact of current,a comparison was done between simulated(EC with RC-elements)and measured overvoltage for18s long pulses at60%SOC at different temper-atures.The differences between both curves were used to generate a lookup table with adjustment factors for the overvoltage as a function of temperature and current.Moreover it was observed that positive and negative current pulses cause very similar voltage responses.In consequence the symmetry factor˛was set to0.5.4.2.Equivalent circuit with RC-elementsThree parts are necessary for modelling the actual cell voltage. Thefirst one is a block for the calculation of the actual OCV.By integrating the current,the actual SOC is computed and recalcu-lated in the open-circuit voltage by a lookup table.The second one, the ohmic resistance depending on the actual I,T and SOC is approx-imated by a lookup table.The last part is the overvoltages by the RC-elements.For implementing the estimated parameters of the RC-element in the EC model,a correlation between input signal current I and output signal voltage U is required for every RC-element.The cur-rent of this parallel connection is:I=I R+I C.(19) The currentflowing through the resistor and capacitor are defined byI R=UR,(20) I C=C·∂U∂t.(21) Including Eqs.(20)and(21)in Eq.(19),the voltage of the RC-element can be calculated byU=t=tendt=0RI−Udt.(22)In this equation R and C are functions of SOC,T and are gained again by lookup tables.The current I is the time dependent input signal and the actual voltage can be calculated by numeri-cal integration using Eq.(22).As introduced in Section4.1these impedances are corrected by determined BV parameters.Finally, the actual cell voltage is calculated by adding up all three voltages.5354 D.Andre et al./Journal of Power Sources196 (2011) 5349–5356Fig.11.Stepwise discharge,on top EC model with RC-elements,on bottom EC model with Zarc and Warburg elements.4.3.Equivalent circuit with Zarc and Warburg elementThe second modelling was done similarly to the described one.In addition,submodels based on the equations of Section 2.2for the parameter estimation of the Zarc and Warburg approximations were built.Analogous to Fig.11the submodels were connected to a cell model and the actual cell voltage could be computed.Due to increased clarity in the further text,the cell model with RC-elements is abbreviated to RC model and the cell model with Zarc and Warburg element is abbreviated to ZW model.5.ValidationBoth models were validated against different current profiles in order to check their performance in a wide SOC and temperature range.The first validation was carried out to test the models in the whole SOC range by comparing the results of cell characterization tests for simulation and measurement.Moreover,the models were tested and analysed for several cycling profiles and finally validated against data recorded during a hybrid electrical vehicle (HEV)drive.Since the computation time plays an important role regarding applicability decisions,a summary of the computation times for all profiles is given in Table 1.The more complex ZW model with in total 13RC-elements is by a factor up to four slower than the simple model with just three RC-elements.Table 1Comparison of computation times for different current profiles.ProfileRC model (s)ZW model (s)Factor Capacity test (∼10,000s)97179 1.8Stepwise discharge (∼12,000s)101182 1.8Test cycle T =−20◦C (∼6100s)4096 2.4Test cycle T =12◦C (∼6100s)79166 2.1Test cycle T =50◦C (∼6100s)58231 4.0HEV cycle (∼2250s)411052.6However,for most profiles the computation time is just doubled and even for the more complex model the simulation time is always below 5%of the real time.5.1.Stepwise dischargeThe first validations were done for typical cell characterization tests such as cell charging and measurement of cell capacity.The result of the cell discharge in steps of 10% SOC for measurement and simulation are shown in Fig.12.It can be observed that both models were able to predict cell voltage with a high quality until a SOC of 10%.From 10%to 0%the cell voltage is dropping down,since the voltage reaches the end of discharge voltage limit.Both models are not able to simulate this phenomenon,since the Butler–Volmer coefficient ˛is probably varying at low SOC.In order to compare the results of both models,the mean value of the absolute error |ε|,the maximum error εmax as well as the sum of squared errors (SSE)between measured and simulated cell voltage are given in addition in all figures.Both models show a similar distribution of voltage deviations and have a very comparable performance with a mean error of about 8mV.No difference can be seen for the SSE,indicating the same quality of simulation for both models.Moreover a maximum error of 27%exists,but is occurring just for a negligible number of measurement points at very low SOC.5.2.Test cycleThe next validations were done against drive cycles at five dif-ferent temperatures measured in the laboratory.Only the results for 12◦C are shown which are representative for the observations at other temperatures.The test cycle consists of a mix of pulses,crankings and drive data for a period of 1.7h.Fig.13shows the different grade of resolution for the comparison of simulation and measurement.Therefore in a second figure (Fig.14)just a time slot of the first 20min is shown.D.Andre et al./Journal of Power Sources196 (2011) 5349–53565355Fig.12.Test cycle measurement and simulation.Both models showed again a very satisfying agreement with the measured values.Especially,the zoom in Fig.13shows that even the simple model is able to represent fast voltage variations within few seconds very well.The error diagram shows very simi-lar values and just a small improvement of SSE can be seen for the ZW model.5.3.Drive cycleThe last profile was measured during test drives in South Africa and is very suited to test the models in consideration of high SOC variations( SOC>30%)and temperature variations.By comparing the error distributions in Fig.14it is obvious that the RC model has a wider variation and almost doubled SSE com-pared to the ZW model.Moreover both models underestimate the cell voltage most of the time,especially at SOCs below60%which is probably a consequence of the BV adjustment which is only valid for a SOC of60%.Even if the voltage peaks are not simulated accu-rately,both models show in general a very good agreement with a mean error below20mV and predict therefore the cell performance very accurately.A summary of the simulation quality represented by the mean error for all tests is given in Table2.Except one case the more com-plex ZW model predicts the cell voltage with a higher accuracy.In Fig.13.Test cycle at T=12◦C,on top EC model with RC-elements,on bottom EC model with Zarc and Warburg elements.5356 D.Andre et al./Journal of Power Sources196 (2011) 5349–5356Fig.14.Drive cycle,on top EC model with RC-elements,on bottom EC model with Zarc and Warburg elements.Table 2Comparison of voltage deviations for different current profiles.ProfileRC model (mV)ZW model (mV) ε(%)Capacity test11.110.5 5.4Stepwise discharge 8.37.59.6Stepwise charge 7.77.2 6.5Test cycle T =−20◦C 10.610.60Test cycle T =−8◦C 5.97.7−30.5Test cycle T =12◦C 10.39.58.0Test cycle T =30◦C 8.3 6.719.3Test cycle T =50◦C 7.87.1 2.6HEV cycle18.715.517.1general the improvement of simulation is in the range of 5–20%,but is always below 3mV.6.Results and discussionIn the last section,two different EC models were introduced.First,a simple model based on an EC of three RC-elements and second a more complex model based on Zarc and Warburg ele-ments.The parameters of both ECs were estimated by a fitting for a large number of measured impedance spectra.It was shown that the simple EC was not able to reproduce the measured data even with optimized parameters sufficiently.In opposite,the more advanced EC was reproducing the spectra very accurate.Since for Zarc as well as Warburg elements no Laplace transformation exists,approximations were derived.These gained ECs were implemented in cell models.Afterwards both models were validated against dif-ferent experimental data as cell characterization tests,test cycles and drive cycle.All validations showed that both models predict cell voltage very precisely.Although the simple EC was not able to reproduce the impedance curves,voltage was predicted with a high -parisons of both models evidenced an up to 20%higher mean error for the simple model by a minimum doubled computation speed.However,also the mean error for this model is just in the range ofa few mV.Therefore it can be concluded that the impedance fitting plays a role for the simulation quality,but the influence is just small and voltage can also be predicted accurately by simple EC models.To sum up,both EC models allow a very precisely prediction of battery voltage and battery performance.Thus it is possible to use these battery models for simulations of e.g.consumption,vehicle range,cooling requirement and battery lifetime prognosis.References[1]C.Andrés,C.F.Valerio,P.Franz,Conference Paper 3rd European Ele-Drive Trans-portation Conference,Geneva,2008.[2]V.H.Johnson, A.A.Pesaran,T.Sack,Conference Paper 17th AnnualElectric Vehicle Symposium,Montreal,2000,/docs/fy01osti/28716.pdf.[3]D.Andre,M.Meiler,K.Steiner,C.Wimmer,T.Soczka-Guth,D.U.,Journal ofPower Sources,submitted for publication.[4]C.H.Chen,J.Liu,K.Amine,Journal of Power Sources 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