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C. Kübel
Dr. Christian Kübel
Research Group Leader
0721/608-28970
christian kuebelTda5∂kit edu
Helmholtz Institute Ulm
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Helmholtzstraße 11
89081 Ulm

Phone: +49 (731) 50 34001

http://www.hiu-batteries.de

info∂hiu.kit.edu

Characterization of Battery Materials and Systems

The development of advanced materials for new batteries increasingly focuses on nanostructured composites to combine high electron and ion conductivity for new cathode materials. These nano composites typically exhibit a complex morphology geared to maintain high capacity over extended charging/discharging cycles. The aim of the electron microscopy & spectroscopy group is to characterize the morphology and composition of the active battery materials at the atomic to nanometer scale in 2D and also 3D using a combination of high-resolution imaging (TEM, HAADF-STEM), diffraction (ACOM-STEM), spectroscopy (EELS, EDX) and tomographic techniques to correlate the structure and morphology at different charging states with the cyclic stability. To some extent, this characterization is possible using well-developed ex situ analytical (S)TEM techniques that only need to be optimized to deal with the electron beam sensitivity of most battery materials. However, for a more direct analysis of the structural changes during electrochemical cycling, we are also actively developing new techniques for in situ imaging of micron/nano-sized battery models inside the TEM.

 

1. Lithium distribution in partially delithiated LiFePO4

Understanding the microscopic mechanism of the de/lithiation processes during electrical cycling is crucial for improving the design of battery materials. A major challenge is the experimental detection of the lithium distribution in partially charged/discharged batteries at the nanoscale because of the weak interaction between Li atoms and fast electrons. In our recent work in collaboration with Prof. Poul Norby from Danish Technical University, we applied a STEM diffraction technique (automated crystal orientation mapping (ACOM)) to map the lithiation distribution in a half discharged lithium iron phosphate (LiFePO4/FePO4, LFP/FP) battery. We found that the majority of the nanoparticles are either completely LFP or FP. However, in addition, quite a number of (single crystalline) particles contain both LFP and FP phases with a planar interface (Figure 1.1). According to the crystallographic information provided by ACOM (Figure 1.2), we found that the LFP/FP interface is preferentially orientated normal to the [101] crystalline direction but not the widely speculated [100] or [010] axes. An average 1.5⁰ misorientation between the LFP and FP domains was detected. This implies that in addition to dislocations, lattice tilting plays a role to release the lattice mismatch between LFP and FP. This experimentally confirms the theoretical predictions based on the interfacial strain energy.

Phase distribution in LFP/FP 

Figure 1.1: (a) ACOM-STEM Phase map of LFP (green) and FP (red) based on the crystallographic difference between both systems. (b) Phase map obtained by EFTEM-SI at the Fe-L3,2 edge (Fe valance state map) (LiFePO4: green, FePO4: red). (c) ACOM-TEM crystal orientation map. The inverse pole figure color coding is given as inset. (d) Bright-field image of the same area as c. The white boxes in a,b and c and the red box in d indicate same particle for visual guidance.

Interface Orientation in LFP/FP single crystals LFP/FP Interface Orientation Distribution

Figure 1.2: (a) ACOM phase and orientation maps of single crystalline particles with an FP/LFP interface and (b) the corresponding statistical analysis of the orientation distribution of the interface shown as orientation density in the inverse pole figure.

Spectroscopic techniques (energy filtered TEM) were applied to analyze the same sample area. The lithium distribution was analyzed 1) mapping the iron oxidation state using the Fe-L3,2 edge, 2) using the Li-K/Fe-M edges, 3) looking at the dielectric function by Kramers-Kronig analysis and 4) based on the plasmon center position. From a methodology point of view, this enabled a direct test of the consistency of the crystallography (ACOM) and oxidation/electronic states (EFTEM/EELS). The maps obtained by all methods showed excellent agreement with each other. A comprehensive comparison of all methods is done in terms of reliability, information content, dose level, acquisition time and signal quality (Table 1). The latter three are relevant for the design of in situ experiments with beam sensitive Li-ion battery materials.

Low-loss EFTEM imaging of the LFP/FP phase distribution

Figure 1.3: EFTEM phase maps (a) from Li-K & Fe-M signals in (b), (c) according to the dielectric functions shown in (d) computed by Kramers-Kronig equation from the signal caused by interband transitions. (e) Volume plasma center map. (f) low-loss spectra of LFP, FP and carbon substance.

 

 Methods  Energy rnage [eV]
 Dose [105 e nm-2]
 Aquisition Time [min]
 Information
 Fe-L3  696 - 720  16  50  Fe valence state
 Li-K / Fe-M
 50 - 66  4.2  13  Fe valence and Li environment
 Kramers-Kronig  -4 - 30
 1.6  5  Dielectricity & optical properties
 Plasma Center
 23 - 28
 0.31  < 1
 Charge density
 ACOM    3.7  45  Crystallography and orientations relating to the phase interface
Table 1: Comparison of LFP/FP phase mapping methods in terms of acquisition dose, acquisition time and information contents (for a 500x500 pixel map with 6 nm pixel size)

 

Details have been published at

  • Comprehensive analysis of TEM methods for LiFePO4/FePO4 phase mapping: spectroscopic techniques (EFTEM, STEM-EELS) and STEM diffraction techniques (ACOM-TEM), X. Mu, A. Kobler, D. Wang, V.S.K. Chakravadhanula, S. Schlabach, D.V. Szabó, P. Norby, C. Kübel, Ultramicroscopy, 2016, 170, 10-18; DOI: 10.1016/j.ultramic.2016.07.009.

 

EU Hi-C

This project has been third-party funded by the European Union through the 7th framework program for research, technological development and demonstration under grant agreement No. 608575.

 

2. Fluoride Ion Batteries

The increasing demand for the performance of energy storage systems is driving the search for alternative battery chemistries beyond Lithium ion batteries (LIBs). Na-, Mg-, Al-, Cl-, K- and F-ion batteries have been introduced as alternative electrochemical systems. Rechargeable batteries based on a fluoride anion shuttle are a promising with energy densities of more than 5000 WhL-1 (50% above the theoretical capacity of the Li air cell). The fluoride ion battery, based on a solid-state electrolyte, is currently developed in the group of Prof. Max Fichtner at the KIT. Figure ‎2.1 shows a schematic of a fluoride ion battery, illustrating the cycling process. The cell consists of a metal (Mʹ) electrode as anode and a metal fluoride (MFx) electrode as cathode in the charged state. During discharging, fluoride anions (F-) will migrate from the cathode (MFx) to the anode (Mʹ) through the electrolyte forming a metal fluoride MʹFx at the anode. At the same time, the electrons provide the work in the external circuit moving from anode to cathode. The equations of the corresponding cathodic and anodic reactions that describe the discharging process are as follows:

x e-+ MFx → M+ x F- (at cathode)
x F-+ M' → M' Fx+ x e- (at anode) ‎

Understanding the compositional, structural and morphological changes occurring at the electrodes during cycling is essential to improve the performance of fluoride ion batteries. Therefore, TEM has been chosen to study all-solid-state fluoride ion batteries ex situ and in situ.

Schematic Fluoride Ion Battery
 

Figure 2.1: Schematic of Fluoride ion battery

 

2.1. Ex situ TEM studies of fuoride ion batteries

In collaboration with the group of Prof. Max Fichtner, interfacial studies were performed by TEM to understand the structural changes at the cathode-electrolyte and anode-electrolyte interfaces, providing new insight into the conversion reaction as well as the degradation mechanism of fluoride ion batteries. The fluoride ion battery consisted of a CuF2 composite as cathode, La0.9Ba0.1F2.9 as an electrolyte, and a La-sheet as anode. The electrochemical cycling was performed at an elevated temperature of 150 ˚C by applying a current density of 10 mA cm-2. Three different states of the system have been studied, as-prepared, discharged, and recharged. Our FIB was used to lift out two lamellae from each pellet at the electrodes-electrolyte interfaces. HRTEM analysis of the cathode confirmed the formation of Cu metal after discharging as a result of CuF2 reduction, while the copper fluoride was formed after recharging, validating the concept of the fluoride ion battery (Figure 2.2). Moreover, The TEM investigation of the anode-electrolyte interface revealed a structural variation upon cycling with the formation of intermediate layers (Figure 2.3) consisting of LaF3 and La2O3 after discharging. During recharging LaOF was irreversibly formed providing one explanation for the reduced capacity of the battery after recharging (Figure 2.3d).

HRTEM images and corresponding FFTs of cathode       Anode-electrolyte interface after discharging

Figure 2.2:HRTEM images and corresponding FFTs of cathode.

Figure 2.3: (a) STEM-EDX map of the anode-electrolyte interface after discharging, (b, c) HRTEM images and corresponding FFTs from an intermediate layer formed at the anode-electrolyte interface after discharging, (d) SAED pattern taken from the intermediate layer formed at the anode-electrolyte interface after discharging.

Details have been published at
  • Reversible CuF2 as cathode for secondary Fluoride Ion Batteries
    D. Tho Thieu, M. H. Fawey; H. Bhatia, T. Diemant, V. S. K. Chakravadhanula, R. Jürgen Behm, C. Kübel, M. Fichtner Advanced Functional Materials 2017 27, 1701051, DOI:10.1002/adfm.201701051.

 

2.2 In situ TEM studies of fluoride ion batteries

In addition to the ex situ TEM analysis shown above, we are developing new preparation and analysis approaches to follow the structural changes in the micron-sized all-solid-state batteries and half-cells in situ using TEM techniques. The FIB has been used to cut a thin cross-section from an all-solid-state battery that is then mounted and contacted to the electrical contacts of a MEMS device (Figure 2.4). The MEMS device, carrying the micron-sized battery, is transferred under (close to) inert conditions to an Aduro sample holder in the TEM for in situ cycling (Figure 2.5).

In situ TEM battery 

Figure ‎2.4: SEM images of (a) blank MEMS device (Protochips E-AEK11) with a 50 µm wide separation between Pt electrical contacts, and (b) an actual micron-sized battery mounted on a MEMS device.

 

 

In situ TEM holder - Fusion

Figure 2.5: An Aduro sample holder from Protochips company for in situ TEM electrical biasing, heating up to 1200 °C and electrothermal analysis. (*) http://www.protochips.com/products/fusion/.

 

The batteries that have been studied by in situ TEM are all-solid-state fluoride ion batteries. We have performed a first successful in situ cycling experiments for two systems of all-solid-state fluoride ion batteries, where reasonable I-V charging-discharging curves have been obtained. Moreover, the structural and compositional changes during cycling were imaged. The two systems that are cycled in situ TEM are:

  • A half-cell consisting of Bi/La0.9Ba0.1F2.9/C as electrode and La0.9Ba0.1F2.9 as solid electrolyte. The half-cell was cycled by applying a sweep voltage between 0 V and 3 V. The formation of BiF3 and BiO0.1F2.8 at the cathode after charging was confirmed by HRTEM and SAED, which were absent in the as-prepared state (Figure 2.6).
  • A full cell consisting of Cu/C as cathode composite, Mg/MgF2/La0.9Ba0.1F2.9/C as anode composite, and La0.9Ba0.1F2.9 as solid electrolyte. The full cell battery was cycled by applying a sweep voltage between 0 V and 3.5 V. The formation of CuF2 after charging was confirmed from the HRTEM images, which was not present in the as-prepared state (Figure 2.7).

 

In situ TEM Half Cell 

Figure ‎2.6: (a) Cyclic voltammetry curve of Bi/La0.9Ba0.1F2.9 half-cell obtained during the 1st charge, (b, c) HRTEM images and corresponding FFTs of the electrode before cycling, (d, e) HRTEM images and corresponding FFTs of the electrode after charging. 

 

In situ TEM full cell 

Figure 2.7: (a) Cyclic voltammetry curves of Cu/La0.9Ba0.1F2.9/MgF2 full cell, (b-d) morphological changes of the cathode-electrolyte interface before cycling, after 1st cycle and after 2nd charging; showing Cu coarsening, void formation and finally delamination at the cathode-electrolyte interface.

 

Details have been published at
  • In situ TEM Studies of Micron-sized All-solid-state Fluoride Ion Batteries: Preparation, Prospects, and Challenges
    Mohammed Hammad Fawey, Venkata Sai Kiran Chakravadhanula, Munnangi Anji Reddy, Carine Rongeat, Torsten Scherer, Horst Hahn, Maximilian Fichtner, and Christian Kübel
    Microscopy Research and Technique 2016, 79, 615–624, DOI:10.1002/jemt.22675.

 

 

3. Metal fluorides as conversion electrodes in lithium ion batteries

In collaboration with Prof. Max Fichtner's group, we have characterized the structure of Fe/LiF/C conversion electrodes used as cathode materials in lithium-ion batteries. The conversion materials prepared by pyrolysis of ferrocene with LiF initially consist of iron (and some iron carbide) nanoparticles with a thin graphitic shell, interconnected by MWCNTs (Fig. 3.4). Charging leads to the formation of FeF2/C or FeF3/C nanoparticles with the graphitic shell still present. Both, the graphitic shell and the MWCNTs are crucial for a good cyclic behavior with the graphitic shell presumably responsible for the cyclic stability of the iron nanoparticles and the MWCNTs ensuring electrical contact through the electrode.   

TEM Characterization of Battery Materials

Fig. 3.4: a) BF-TEM overview image of aggregates of Fe/C nanoparticles with LiF in between and interconnected by MWCNTs; b/c) HRTEM images of the Fe/C nanoparticles consisting of an α-iron core and a shell typically of in-situ TEM characterization of up to 3-5 graphene layers.

 

Details have been published at

  • Modified synthesis of [Fe/LiF/C] nanocomposite, and its application as conversion cathode material in lithium batteries, R. Prakash et al. Journal of Power Sources 196 (2011) 5936-5944; DOI: 10.1016/j.jpowsour.2011.03.007.
  • A ferrocene-based carbon-iron lithium fluoride nanocomposite as a stable electrode material in lithium batteries R. Prakash, A.K. Mishra, A. Roth, C. Kübel, T. Scherer, M. Ghafari, H. Hahn, M. Fichtner J. Mat. Chem., 2010, 20(10), 1871-1876; DOI:10.1039/B919097J
  • Carbon encapsulated-iron lithium fluoride nanocomposite as high cyclic stability cathode material in lithium batteries R. Prakash, C. Kübel, M. Fichtner Materials Challenges in Alternative and Renewable Energy, G. Wicks, et al. (Eds.), Ceram. Trans., 2011, 224, 173-182, Wiley Inc., New Jersey; DOI: 10.1002/9781118019467.ch18
  • Synthesis of [Co/LiF/C] nanocomposite and its application as cathode in lithium-ion batteries C. Wall, R. Prakash, C. Kübel, H. Hahn, M. Fichtner J. Alloys Comp., 2012, 530, 121-126; DOI: 10.1016/j.jallcom.2012.03.080