Advanced Fluoride-Based Materials for Energy Conversion PDF
Preview Advanced Fluoride-Based Materials for Energy Conversion
Advanced Fluoride-Based Materials for Energy Conversion Edited by Tsuyoshi Nakajima Department of Applied Chemistry Aichi Institute of Technology Yakusa, Toyota, Japan Henri Groult Sorbonne Universités, UPMC Univ. Laboratoire PHENIX CNRS, Paris, France AMSTERDAM • BOSTON • HEIDELBERG • LONDON • NEW YORK • OXFORD PARIS • SAN DIEGO • SAN FRANCISCO • SINGAPORE • SYDNEY • TOKYO Elsevier Radarweg 29, PO Box 211, 1000 AE Amsterdam, The Netherlands The Boulevard, Langford Lane, Kidlington, Oxford OX5 1GB, UK 225 Wyman Street, Waltham, MA 02451, USA Copyright © 2015 Elsevier Inc. All rights reserved. No part of this publication may be reproduced or transmitted in any form or by any means, electronic or mechanical, including photocopying, recording, or any information storage and retrieval system, without permission in writing from the publisher. 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British Library Cataloguing in Publication Data A catalogue record for this book is available from the British Library Library of Congress Cataloging-in-Publication Data A catalog record for this book is available from the Library of Congress ISBN: 978-0-12-800679-5 For information on all Elsevier publications visit our web site at http://store.elsevier.com/ Contributors Bruno Ameduri Institut Charles Gerhardt, Ingénierie et Architectures Macromoléculaires, UMR CNRS 5253, Ecole Nationale Supérieure de Chimie de Montpellier, Montpellier, France Khalil Amine Chemical Sciences and Engineering Division, Argonne National Laboratory, Lemont, IL, USA Ramin Amin-Sanayei Arkema Inc, King of Prussia, PA, USA Ahmed Bahloul Laboratoire des Matériaux et Systèmes Électroniques, Centre Universitaire de Bordj Bou Arréridj, Bordj Bou Arréridj, Algeria T. Böttcher School of Engineering and Science, Jacobs University GmbH, Bremen, Germany Emmanuel Briot Sorbonne Universités, UPMC Univ., Laboratoire PHENIX, CNRS, Paris, France S. Cadra CEA/DAM, Le Ripault, Monts, France Benjamin Campagne Institut Charles Gerhardt, Ingénierie et Architectures Macromoléculaires, UMR CNRS 5253, Ecole Nationale Supérieure de Chimie de Montpellier, Montpellier, France Zonghai Chen Chemical Sciences and Engineering Division, Argonne National Laboratory, Lemont, IL, USA Mouad Dahbi Department of Applied Chemistry, Tokyo University of Science, Tokyo, Japan; Elements Strategy Initiative for Catalysts and Batteries, Kyoto University, Kyoto, Japan A. Darwiche IPREM-ECP CNRS UMR 5254, Pau, France Ghislain David Institut Charles Gerhardt, Ingénierie et Architectures Macromoléculaires, UMR CNRS 5253, Ecole Nationale Supérieure de Chimie de Montpellier, Montpellier, France R. Dedryvère ICG-AIME, Université Montpellier 2, Montpellier, France M. Dubois Institute of Chemistry of Clermont-Ferrand, University of Blaise Pascal, Aubiere Cedex, France D. Farhat PCM2E, Université F. Rabelais, Parc de Grandmont, Tours, France Maximilian Fichtner Helmholtz Institute Ulm for Electrochemical Energy Storage (HIU), Helmholtzstr, Ulm, Germany F. Ghamouss PCM2E, Université F. Rabelais, Parc de Grandmont, Tours, France xiii xiv Contributors Henri Groult Sorbonne Universités, UPMC Univ., Laboratoire PHENIX, CNRS, Paris, France K. Guérin Institute of Chemistry of Clermont-Ferrand, University of Blaise Pascal, Aubiere Cedex, France Rika Hagiwara Department of Fundamental Energy Science, Graduate School of Energy Science, Kyoto University, Kyoto, Japan Wensheng He Arkema Inc, King of Prussia, PA, USA Christian M. Julien Sorbonne Universités, UPMC Univ., Laboratoire PHENIX, CNRS, Paris, France N. Kalinovich School of Engineering and Science, Jacobs University GmbH, Bremen, Germany O. Kazakova School of Engineering and Science, Jacobs University GmbH, Bremen, Germany Jae-Ho Kim Headquarters for Innovative Society-Academia Cooperation, Fukui University, Fukui, Japan Shinichi Komaba Department of Applied Chemistry, Tokyo University of Science, Tokyo, Japan; Elements Strategy Initiative for Catalysts and Batteries, Kyoto University, Kyoto, Japan Sandrine Leclerc Sorbonne Universités, UPMC Univ., Laboratoire PHENIX, CNRS, Paris, France Young-Seak Lee Department of Applied Chemistry and Biological Engineering, Chungnam National University, Daejeon, Republic of Korea D. Lemordant PCM2E, Université F. Rabelais, Parc de Grandmont, Tours, France B. Lestriez Institut des Matériaux Jean Rouxel (IMN), CNRS UMR 6502, Université de Nantes, Nantes, France H. Martinez ICG-AIME, Université Montpellier 2, Montpellier, France Kazuhiko Matsumoto Department of Fundamental Energy Science, Graduate School of Energy Science, Kyoto University, Kyoto, Japan Alain Mauger Sorbonne Universités, UPMC Univ., Laboratoire PHENIX, CNRS, Paris, France; UPMC Univ. Paris 06, Institut de Minéralogie et Physique de la Matière Condensée, Paris, France L. Monconduit IPREM-ECP CNRS UMR 5254, Pau, France Tsuyoshi Nakajima Department of Applied Chemistry, Aichi Institute of Technology, Yakusa, Toyota, Japan Madeleine Odgaard IRD Fuel Cells A/S, Kullinggade, Svendborg, Denmark M. Ponomarenko School of Engineering and Science, Jacobs University GmbH, Bremen, Germany Ana-Gabriela Porras-Gutierrez Sorbonne Universités, UPMC Univ., Laboratoire PHENIX, CNRS, Paris, France Contributors xv Munnangi Anji Reddy Helmholtz Institute Ulm for Electrochemical Energy Storage (HIU), Helmholtzstr, Ulm, Germany G.-V. Röschenthaler School of Engineering and Science, Jacobs University GmbH, Bremen, Germany Soshi Shiraishi Graduate School of Science and Technology, Gunma University, Kiryu, Japan Masayuki Takashima Department of Materials Science & Engineering, Faculty of Engineering, University of Fukui, Fukui, Japan Osamu Tanaike Research Center for Compact Chemical System, National Institute of Advanced Industrial Science and Technology, Sendai, Japan K. Vlasov School of Engineering and Science, Jacobs University GmbH, Bremen, Germany M. Winter MEET—Münster Electrochemical Energy Technology, Westfälische Wilhelms-Universität, Münster, Germany Susumu Yonezawa Headquarters for Innovative Society-Academia Cooperation, Fukui University, Fukui, Japan; Department of Materials Science & Engineering, Faculty of Engineering, University of Fukui, Fukui, Japan Zhengcheng Zhang Chemical Sciences and Engineering Division, Argonne National Laboratory, Lemont, IL, USA W. Zhang ICG-AIME, Université Montpellier 2, Montpellier, France Preface The present book summarizes recent progress of fluoride-based materials for lithium and sodium batteries, fuel cells, and capacitors. These electric energy- generating devices have been widely used for many objectives. In particular, they are important energy sources not only for hybrid and electric vehicles, but also for our daily lives. To save petroleum resources and suppress CO genera- 2 tion, the social demand for electrochemical devices generating electric energy has been increasing. Hybrid cars are now popular in our society and fuel cell cars will be soon sold. Fuel and solar cells are also found in many buildings and houses. Lithium batteries are of course important energy sources for many kinds of electronic devices. Among various materials used as electrodes, elec- trolytes, membranes, and so on for lithium and sodium batteries, fuel cells and capacitors, fluorine-containing compounds have exhibited high functions not found in other materials. Fluorine atom with a small size has the highest electronegativity and small polarizability, making strong and stable chemical bonds with other elements. Since fluorine gas (F ) has a small dissociation 2 energy (155 kJ mol−1), the reactivity of F with other compounds and single 2 substances is very high. Not only F , but also NF and ClF are important fluo- 2 3 3 rinating agents used for the preparation of many kinds of fluorine compounds. Because of these properties of fluorine, inorganic and organic fluorine com- pounds and fluoropolymers are now employed for lithium batteries, fuel cells, and capacitors. The use of graphite fluoride as a cathode material of primary lithium battery was realized about 40 years ago. Since then, graphite fluoride has been used for primary lithium battery as an excellent cathode. Commer- cialization of Li/(CF) battery revealed the usefulness of fluorine compounds n as energy materials. Polytetrafluoroethylene (PTFE) has been also used for fuel cells to control the surface property of electrodes. Recently, many kinds of fluorine-containing materials are being examined as new electrodes, elec- trolytes, additives, membranes, and binders. Surface modification is one of the convenient methods to improve the functions of electrode materials because F and other fluorinating agents have high reactivity and can easily modify 2 the surface structures and composition of solid materials. Nowadays many inorganic, organic, and polymer fluorine chemists are working to develop new materials for batteries and capacitors. “Energy” is now one of the important discussion themes at international fluorine symposiums and conferences. The present book provides advanced information on fluorinated materials used as xvii xviii Preface energy conversion materials, being quite useful for researchers, graduate stu- dents, and engineers in universities, research institutes, and industries. Tsuyoshi Nakajima (Aichi Institute of Technology, Japan) Henri Groult (University of Pierre and Marie Curie, CNRS, France) Chapter 1 High Performance Lithium-Ion Batteries Using Fluorinated Compounds Zonghai Chen, Zhengcheng Zhang and Khalil Amine Chemical Sciences and Engineering Division, Argonne National Laboratory, Lemont, IL, USA Chapter Outline 1.1 Introduction 1 1.3 F luorinated Redox Shuttles 13 1.2 Stabilization of Lithiated 1.4 H igh Voltage Electrolytes 19 Anodes 2 1.5 C losing Remarks 29 1.2.1 Modification of Acknowledgments 29 SEI Layer 5 References 30 1.2.2 Artificial SEI Layer 7 1.1 INTRODUCTION Lithium-ion batteries have been the dominant energy storage technology for powering modern portable electronics. There is also a global effort on R&D of advanced lithium-ion batteries for propulsion and stationary applications in smart grids. The major technological barriers that hinder the realization of these emerging applications include (1) high cost, (2) insufficient life, (3) insufficient energy density, and (4) intrinsically poor safety characteristics. These barriers can be partially tackled by developing advanced electrode materials with a bet- ter structural stability, developing materials with higher energy density, and/or using low-cost starting materials and manufacturing processes. High energy- density materials are of great interest since they can lead to an overall reduction in the battery size, resulting in a large saving on other materials like the elec- trolyte and separator. These barriers can also be addressed by developing func- tionalized electrolytes that suppress the side reactions between the electrode materials and the electrolytes; these side reactions are the major contributors to the degradation of battery performance. The current lithium-ion batteries generally use graphitic carbons as the anode material, a lithium transition metal oxide as the cathode material, and a solution Advanced Fluoride-Based Materials for Energy Conversion. http://dx.doi.org/10.1016/B978-0-12-800679-5.00001-4 Copyright © 2015 Elsevier Inc. All rights reserved. 1 2 Advanced Fluoride-Based Materials for Energy Conversion of LiPF in a blend solvent of alkyl carbonates as the electrolyte. The electrolyte 6 in the battery is used as the lithium-ion conducting medium to transport lithium ions between the anode and cathode. The chemical–electrochemical reactions leading to performance degradation, as well as a potential safety hazard, mostly occur at the interface between the electrode material and the nonaqueous elec- trolyte, where the electrolyte components can act as either the reactant or the dilution medium that promotes detrimental reactions [1,2]. In an ideal system, the solvent should have a combination of several physical–chemical properties. First, it should be able to dissolve a fairly high concentration of lithium salts for high lithium-ion conductivity. Second, the energy level of the highest occupied molecular orbital (HOMO) of the solvents should be low enough for good resis- tance to oxidation by the delithiated cathode. Third, the energy level of the lowest unoccupied molecular orbital (LUMO) of the solvents should be high enough to prevent the reduction by lithiated anode materials. So far, an electrolyte that meets the above three requirements has not been identified. For instance, the LUMOs of currently used carbonates are substantially lower than the Fermi energy level of lithium, and hence, they are thermodynamically incompatible with lithium metal and lithiated graphite. The long-term stability of lithiated graphite with the presence of nonaqueous electrolytes can only be kinetically achieved with the presence of the solid-electrolyte interphase (SEI) [3–5], which is a thin layer of an organic–inorganic composite deposited on the surface of a graphitic electrode and acts as a kinetic barrier to protect the lithiated graphite from rapid reaction with the nonaqueous electrolyte. Recently, a massive effort has been devoted to developing cathode materials with high specific capacity and high voltage to meet the energy requirements for plug-in hybrid electric vehicles and full electric vehicles [6–10]. These R&D efforts have pushed the working potential of the cathode materials beyond the thermodynamic limit of the carbonate solvents, and an advanced electrolyte is highly desired to enable high-voltage cathodes [11,12]. Even within a well-characterized lithium-ion chemistry, the working potential of electrode materials can be driven beyond the electrochemically stable window of solvents during overcharge abuse, which can occur during the normal operation of an off-balance lithium-ion battery pack [13–16]. In this chapter, emphasis will be placed on advanced electrolytes with fluo- rinated components, including (1) advanced electrolyte additives that stabilize lithiated anodes; (2) fluorinated redox shuttles for overcharge protection and automatic capacity balance of the lithium-ion battery pack; and (3) advanced high-voltage electrolytes comprising fluorinated solvents. 1.2 STABILIZATION OF LITHIATED ANODES Graphitic materials have been the dominant anode material for state-of-the-art lithium-ion technology. However, it is also well known that the lower cutoff potential of lithiated graphite can be as low as 0.1 V versus Li+/Li, which is far below the standard redox potential of carbonates used for lithium-ion batteries. High Performance Lithium-Ion Batteries Chapter | 1 3 The long-term compatibility between the lithiated graphite and the electrolyte solvents is kinetically achieved with the presence of an SEI layer that acts as a physical barrier to prevent the direct exposure of the lithiated graphite to non- aqueous electrolytes. Figure 1.1 schematically shows the SEI formation mecha- nism during the initial lithiation of a graphitic anode. In general, the open circuit potential of the anode in a freshly prepared lithium-ion cell is about 3.0 V versus Li+/Li. During the initial charge (also called the formation stage) of a fresh lithium-ion cell, the potential of the graphitic anode decreases with the lithia- tion process. The lithium salt, typically LiPF , starts to decompose at a potential 6 below 1.5 V versus Li+/Li [17,18]. Part of the decomposition product, mostly inorganic components, deposits on the graphite surface while other components like PF promote the electrically triggered polymerization reaction of ethylene 5 carbonate (EC) that forms a flexible layer, mostly organic components, on top of the inorganic layer. This layer of organic–inorganic thin film, or SEI layer, gives a long life to lithium-ion batteries using graphitic anodes. The thermal and electrochemical stability of this SEI layer will determine the electrochemical performance of the batteries using graphitic anodes. Zheng et al. [5] investigated the capacity loss of half cells comprising mesocarbon microbeads (MCMB) electrodes during storage experiments at various temperatures, and found that the capacity loss increased exponentially with the storage temperature. Kinet- ics study revealed that the process leading to the capacity loss had a fairly low activation energy of 39.7 kJ mol−1. It was concluded that the thermal instability of the SEI layer was a contributor to the capacity loss in lithium-ion cells stored or operated at elevated temperatures. Alternatively, Levi et al. [19] investigated the same issue by tracing the self-discharge process of the graphitic anodes; this process was attributed to the continuous reaction between the lithiated graphite (cid:19)(cid:17)(cid:19) (cid:16)(cid:19)(cid:17)(cid:20) (cid:47)(cid:76) (cid:38) (cid:91) (cid:25) (cid:57) (cid:75)(cid:18)(cid:16)(cid:19)(cid:17)(cid:21) (cid:36) (cid:80) (cid:57)(cid:15)(cid:3)(cid:16)(cid:19)(cid:17)(cid:22) (cid:71) (cid:54)(cid:40)(cid:44) (cid:52)(cid:18) (cid:71) (cid:16)(cid:19)(cid:17)(cid:23) (cid:16)(cid:19)(cid:17)(cid:24) (cid:19)(cid:17)(cid:19) (cid:19)(cid:17)(cid:24) (cid:20)(cid:17)(cid:19) (cid:20)(cid:17)(cid:24) (cid:21)(cid:17)(cid:19) (cid:21)(cid:17)(cid:24) (cid:38)(cid:72)(cid:79)(cid:79)(cid:3)(cid:83)(cid:82)(cid:87)(cid:72)(cid:81)(cid:87)(cid:76)(cid:68)(cid:79)(cid:3)(cid:89)(cid:86)(cid:17)(cid:3)(cid:47)(cid:76)(cid:14)(cid:18)(cid:47)(cid:76)(cid:15)(cid:3)(cid:57) FIGURE 1.1 Schematic showing the formation of solid electrolyte interphase during the initial lithiation of a graphitic anode. SEI, solid-electrolyte interphase.
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