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  • The Electrochemical Society  (14)
  • 1
    Online Resource
    Online Resource
    The Electrochemical Society ; 2014
    In:  ECS Meeting Abstracts Vol. MA2014-02, No. 21 ( 2014-08-05), p. 1063-1063
    In: ECS Meeting Abstracts, The Electrochemical Society, Vol. MA2014-02, No. 21 ( 2014-08-05), p. 1063-1063
    Abstract: Introduction Core-shell structured catalyst is a promising candidate for the decrease in usage amount of an expensive Pt cathode catalyst for PEFCs. Adzic and his co-workers demonstrated that carbon supported Pd core-Pt shell structured catalyst (Pt/Pd/C) exhibits higher ORR performance relative to that of a commercial Pt/C catalyst [1] and that the Pd core dissolves out during an accelerated durability test (ADT) using potential cycling [2] . We have recently reported that ORR activity of the Pt/Pd/C catalyst synthesized with a modified Cu under potential deposition (Cu-UPD) and a Pt replacement processes is enhanced with the ADT performed at 80°C [3, 4]. After the ADT, morphology of the Pt/Pd/C catalyst changed into spherical shape and mean diameter of the catalyst decreased associated with an oxidative dissolution of the Pd core. It was presumed that the enhancement of the ORR activity was caused from decrease in number of low-coordinated Pt atoms by rearrangement of the surface Pt atoms with the ADT. Interestingly, the core-shell structure was retained even after the ADT. In this study, carbon supported PtPd alloy catalyst (PtPd/C) was prepared through one-pot synthesis and change in the ORR activity of the catalyst by the ADT at 80°C was investigated in comparison with that of the Pt/Pd/C catalyst. Experimental Pt/Pd/C catalyst was synthesized with modified Cu-UPD and Pt replacement processes [3]. Carbon supported Pd core (Pd/C, 4.2 nm, 30 wt.%) was dispersed 0.05 M H 2 SO 4 containing 0.01 M CuSO 4 and stirred under Ar atmosphere with co-existence of Cu mesh, by which Cu shell was formed on the Pd core surface. Then, the Cu mesh was removed and K 2 PtCl 4 was added to replace the Cu shell with the Pt one, giving the Pt/Pd/C catalyst. PtPd/C alloy catalyst was prepared with one-pot reduction method. H 2 PtCl 6 and Na 2 PdCl 4 were dissolved into DI water and pH of the solution was adjusted at 3.5 by NaOH, followed by addition of a carbon support (Ketjen black EC 300J). The solution was stirred at 60°C in air and NaBH 4 was added in drop-wise, forming the PtPd/C alloy catalyst [5]. Catalysts were characterized with TG, XRD, XRF, TEM, TEM-EDX and CV. ORR activities of the catalysts were evaluated with RDE technique in O 2 saturated 0.1 M HClO 4 at 25°C. ADT was conducted using a rectangular wave potential cycling (0.6 V (3 s)-1.0 V (3 s) vs . RHE, 10,000 cycles) in Ar saturated 0.1 M HClO 4 at 80°C. Results and Discussion XRD patterns of the catalysts are shown in Fig. 1. All samples exhibited characteristic diffraction patterns of fcc structure. In PtPd/C catalyst, composition was Pt 51 Pd 49 (in at.%) and (220) diffraction peak angle was close to that of the Vegard’s law (dotted blue arrow), indicating that Pt and Pd are well-mixed and form alloy particle. In Pt/Pd/C catalyst, (220) diffraction peak angle did not change after Pt shell formation and peak symmetry was retained. TG and XRF analyses showed that the Pt shell formed on the Pd core surface corresponds to 1.1 times of Pt monolayer. TEM images of the catalysts are depicted in Fig. 2. In PtPd/C catalyst, small size PtPd NPs disappeared after ADT and mean diameter of the catalyst increased. On the contrary, morphology of Pt/Pd/C catalyst changed into a spherical shape with ADT and mean diameter decreased. XRF compositional analysis revealed that 41 % and 70 % Pd were dissolved out from the PtPd/C and the Pt/Pd/C catalyst, respectively, after the ADT. Figure 3 summarizes ORR mass activity of the catalysts in comparison with that of a commercial Pt/C catalyst (TEC10E50E, TKK). Initial PtPd/C catalyst showed the highest ORR mass activity due to its high specific activity. After ADT at 80°C, ORR mass activity of Pt/Pd/C catalyst was largely enhanced (3.0-fold of Pt/C catalyst). Interestingly, TEM-EDX analysis indicated that core-shell structure was retained even after the ADT, which suggests that the core-shell structure is stable although more than 50 % of the Pd core dissolved out with ADT. ORR mass activity of the PtPd/C alloyed catalyst could be enhanced with suppression of large decrease in electrochemical surface area with ADT. Acknowledgement This work was supported by NEDO Japan. References [1] A. U. Nilekar et al ., Top. Catal ., 46 , 276 (2007). [2] K. Sasaki et al ., Angew. Chem. Int. Ed ., 49 , 8602 (2010). [3] Y. Ikehata et al ., 224 th ECS Meeting, Abstract #1497, San Francisco, USA (2013). [4] H. Daimon et al ., 224 th ECS Meeting, Abstract #1404, San Francisco, USA (2013). [5] K. Okuno et al ., 81 st Japanese Electrochemical Society Meeting, Abstract PFC05, Osaka, Japan (2014).
    Type of Medium: Online Resource
    ISSN: 2151-2043
    Language: Unknown
    Publisher: The Electrochemical Society
    Publication Date: 2014
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  • 2
    Online Resource
    Online Resource
    The Electrochemical Society ; 2012
    In:  ECS Meeting Abstracts Vol. MA2012-02, No. 49 ( 2012-06-04), p. 3454-3454
    In: ECS Meeting Abstracts, The Electrochemical Society, Vol. MA2012-02, No. 49 ( 2012-06-04), p. 3454-3454
    Abstract: Abstract not Available.
    Type of Medium: Online Resource
    ISSN: 2151-2043
    Language: Unknown
    Publisher: The Electrochemical Society
    Publication Date: 2012
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  • 3
    In: ECS Meeting Abstracts, The Electrochemical Society, Vol. MA2008-02, No. 49 ( 2008-08-29), p. 3027-3027
    Abstract: Abstract not Available.
    Type of Medium: Online Resource
    ISSN: 2151-2043
    Language: Unknown
    Publisher: The Electrochemical Society
    Publication Date: 2008
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  • 4
    Online Resource
    Online Resource
    The Electrochemical Society ; 2015
    In:  ECS Meeting Abstracts Vol. MA2015-03, No. 3 ( 2015-07-15), p. 669-669
    In: ECS Meeting Abstracts, The Electrochemical Society, Vol. MA2015-03, No. 3 ( 2015-07-15), p. 669-669
    Abstract: It is now widely recognized that the amount of expensive Pt catalyst in PEFCs should be decreased for cost reduction.  Pd core/Pt shell structured catalyst supported on carbon (Pt/Pd/C) is a strong candidate for improving the utilization of Pt.  It has been also reported that the activity oxygen reduction reaction (ORR) activity of the Pt shell is enhanced by the strain effect of the Pd core [1,2].  Recently, we developed a new synthetic method for carbon supported Pd core/Pt ML shell structured catalyst (Pt/Pd/C) using a modified Cu-UPD process [3] and found that ORR activity of the Pt/Pd/C catalyst was drastically enhanced after a potential cycling accelerated durability test (ADT) [4] .  In this study, we investigated microstructural changes of the Pt/Pd/C catalyst after potential cycling and discussed the mechanism for the enhanced ORR activity.  In addition, we optimized the protocol for potential cycling to further enhance the ORR activity. Pt/Pd/C catalyst was obtained from Pd/C core (4.5 nm, 30 wt.%, Ishifuku Metal Industry) using the modified Cu-UPD method [3].  The Pd/C core and Pt/Pd/C catalyst were characterized by TG, XRD, XRF, TEM, TEM-EDX and CV.  The ORR activity of the catalyst was measured by the RDE technique at 1,600 rpm in O 2 saturated 0.1 M HClO 4 at 298 K.  The ADT was performed using rectangular-wave potential cycling (FCCJ, 0.6 V (3 s)/1.0 V (3 s) vs . RHE for 10,000 cycles) in Ar saturated 0.1 M HClO 4 at 353 K. The ORR activity of the Pt/Pd/C catalyst was enhanced after ADT, showing by 2-fold higher ORR mass activity (512 A/g-Pt) than that of a commercially available Pt/C catalyst (2.8 nm, 46 wt.%, TEC10E50E, TKK).  Morphological changes of the Pt/Pd/C catalyst after ADT is shown in Figure 1.  The average size of the catalyst decreased from 5.6 to 4.9 nm and the catalyst particles changed into spherical particles.  TEM-EDX analysis revealed that the Pd core dissolved out by 73 % and the Pt shell was thickened (to approximately 2.3 ML) after ADT. The microstructural change of the Pt/Pd/C catalyst after ADT is schematically illustrated in Figure 2. The Pd core dissolved out through defects on the Pt shell during ADT.  As a result, the Pt atoms at the shell were rearranged to give a defect-free surface to the Pt shell, by which the number of lower coordinated Pt atoms decreased.  EXAFS analysis revealed that the Pt-Pt bond length decreased after ADT.  It was concluded that the enhanced ORR activity after ADT was caused by a moderately induced compressive strain at the Pt shell, in addition to a decreased number of the lower coordinated Pt atoms. Though the ADT protocol gave an enhanced mass activity (~ x2) to the Pt/Pd/C catalyst, there remains one problem that the electrochemical surface area (ECSA) decreased from 140 initially to 40-50 m 2 /g-Pt after ADT.  Hence we optimized the potential cycling protocol to minimize the decrease in ECSA during ADT.  The optimized protocol (0.4 V (300 s)/1.0 V (300 s) for 60 cycles) gave a high ECSA ( 〉 80 m 2 /g) and a very high ORR mass activity (1002 A/g-Pt, x4 of Pt/C) after potential cycling. Acknowledgment This study was supported by NEDO, Japan. References [1] J. Zhang et al ., J. Phys. Chem. B , 108 (2004) 10955. [2] J. Zhang et al ., Angew. Chem., Int. Ed ., 44 (2005) 2132. [3] Y. Ikehata et al ., The 224 th ECS meeting, Abstract #1497, San Francisco USA, (2013). [4] H. Daimon et al ., The 224 th ECS meeting, Abstract #1404, San Francisco USA, (2013). Figure 1
    Type of Medium: Online Resource
    ISSN: 2151-2043
    Language: Unknown
    Publisher: The Electrochemical Society
    Publication Date: 2015
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  • 5
    Online Resource
    Online Resource
    The Electrochemical Society ; 2014
    In:  ECS Meeting Abstracts Vol. MA2014-02, No. 21 ( 2014-08-05), p. 1135-1135
    In: ECS Meeting Abstracts, The Electrochemical Society, Vol. MA2014-02, No. 21 ( 2014-08-05), p. 1135-1135
    Abstract: Introduction The usage of the expensive Pt cathode catalyst in PEFCs must be reduced for their worldwide commercialization. Core-shell structured catalyst, in which Pt monolayer (Pt ML ) is formed on the other metal core surface, is one of the key technologies for the reduction of the Pt usage. Furthermore, it has been shown that the ORR activity of Pt ML formed on Pd core NPs is enhanced [1, 2]. Conventionally, the Pt ML has been formed on a core surface through Cu under potential deposition (Cu-UPD) followed by Pt replacement reaction. However, the Cu-UPD requires a precise potential control and weight of treated core on glassy carbon (GC) electrode is extremely small (several tens mg). Recently, we have developed a new method for the Pt shell formation which needs no precise potential control and is suitable for scale-up synthesis toward the core-shell structured catalyst (modified Cu-UPD/Pt replacement method [3] ). We further demonstrated that the ORR mass activity of a carbon supported Pd core/Pt shell structured catalyst (Pt/Pd/C) synthesized by the modified Cu-UPD/Pt replacement method is drastically enhanced with an accelerated durability test (ADT) performed at 80°C [3]. TEM observation revealed that the mean diameter of the catalyst decreased and the morphology changed into a spherical shape after the ADT associated with oxidative dissolution of the Pd core. It was presumed that the ORR activity enhancement after the ADT was caused by a rearrangement of the surface Pt atoms and a decrease in Pt atoms with lower coordination numbers. In this study, we tried to correlate the change in ORR activity with the surface micro-structural change in the Pt shell using Bi 3+ cation as a probe, which specifically is adsorbed on the Pt (111) face [4]. Experimental Pt/Pd/C catalyst was synthesized with the modified Cu-UPD/Pt replacement method [3]. Pd/C core and Pt/Pd/C catalyst were characterized with TG, XRF, XRD, TEM and CV. ORR activity of the catalyst was measured by RDE technique in O 2 saturated 0.1 M HClO 4 at 25°C. ADT was performed using a rectangular wave potential cycling (0.6 V (3 s)-1.0 V (3 s) vs . RHE) in Ar saturated 0.1 M HClO 4 at 80°C for 10,000 cycles. The Pt has a fcc crystallographic structure and the (111) face is energetically the most stable. Since Bi 3+ is specifically adsorbed on the (111) face of Pt [4], we selected the cation as a probe for an evaluation of the (111) ratio on the surface. A GC electrode casted with the Pt/Pd/C catalyst was immersed into 0.05 M H 2 SO 4 containing 0.5 mM Bi 2 O 3 to be adsorbed. After washing the GC electrode with DI water, CV was recorded in Ar saturated 0.05 M H 2 SO 4 at 25°C. The amount of the adsorbed Bi 3+ was converted into the surface Pt atomic ratio of the (111) face [4]. Results and Discussion Figure 1 demonstrates the change in ORR specific activity of a commercial carbon supported Pt catalyst (Pt/C, TEC10E50E, TKK) and Pt/Pd/C catalyst before and after the ADT. The specific activity of both catalysts increased after the ADT; however, the enhancement of Pt/Pd/C catalyst was much higher than that of Pt/C as reported previously [3]. Figure 2 depicts changes in CVs of Pt/C and Pt/Pd/C catalysts probed by Bi 3+ before and after the ADT. Initially, the Pt/C catalyst showed Bi 3+ adsorption wave at ca. 0.62 V vs . RHE (emphasized by dotted pink rectangular), which is assigned to adsorption on the Pt(111) terrace. However, the adsorption wave was not observed for the initial Pt/Pd/C catalyst. After the ADT, the Bi 3+ adsorption wave on the Pt/C catalyst decreased, while the wave appeared on the Pt/Pd/C catalyst. Table 1 summarizes the ratio of the Pt(111) area to the total one for each catalyst. The ratio was calculated using the Bi 3+ adsorption and H UPD waves [4]. It should be noted that the surface Pt(111) ratio on the Pt/Pd/C catalyst increased after the ADT. Although the decrease in the ratio for the Pt/C catalyst after the ADT has not been clarified, it is strongly suggested that the surface Pt rearrangement during the ADT influences the ORR activity of the Pt/C and Pt/Pd/C catalysts. Acknowledgement This work was supported by New Energy and Industrial Technology Development Organization (NEDO), Japan. References [1] J. Zhang et al ., J. Phys. Chem. B , 108 , 10955 (2004). [2] J. Zhang et al ., Angew. Chem. Int. Ed ., 44 , 2132 (2005). [3] H. Daimon et al ., 224 th ECS Meeting, Abstract #1404, San Francisco, USA (2013). [4] F. J. Vidal-Iglesias et al ., Phys. Chem. Chem. Phys ., 10 , 1395(2008).
    Type of Medium: Online Resource
    ISSN: 2151-2043
    Language: Unknown
    Publisher: The Electrochemical Society
    Publication Date: 2014
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  • 6
    Online Resource
    Online Resource
    The Electrochemical Society ; 2016
    In:  ECS Meeting Abstracts Vol. MA2016-02, No. 3 ( 2016-09-01), p. 285-285
    In: ECS Meeting Abstracts, The Electrochemical Society, Vol. MA2016-02, No. 3 ( 2016-09-01), p. 285-285
    Abstract: We had reported that an amorphous silicon flake powder (Si LeafPowder®, Si-LP), of which the lateral dimension and the thickness were ~4 μm and 100 nm, respectively, demonstrated superior cycle performances. [1, 2] Cyclability of the Si-LP electrodes was successfully improved by an addition of solid electrolyte interface (SEI)-forming additives such as vinylene carbonate (VC) and fluoroethylene carbonate (FEC). However, the capacity-fading mechanism of the Si-LP electrodes has not been clarified. In order to understand the capacity fading of the Si-LP and effects of additives, variations of impedance components and the morphology changes were investigated. Test electrodes were composed of Si-LP (83.3 wt.%), Ketjen Black (5.6 wt.%) and carboxymethyl cellulose sodium salt (11.1 wt.%), and coated on a Cu foil. The loading of the Si-LP composite was approximately 0.4 mg cm -2 . Electrolytes were 1 M LiPF 6 dissolved in a mixture of ethylene carbonate and diethyl carbonate (EC+DEC, 1:1 by vol.) with and without additive of 10 wt.% VC or FEC. Charge and discharge tests were conducted at C/2 rate in the CC-CV mode between 1.5 and 0.02 V using a two-electrode coin-type cell. The electrochemical impedance spectroscopy (EIS) was performed using a three-electrode cell in which impedance spectra were obtained by applying an AC voltage of 10 mV over the frequency range of 0.03 Hz to 300 kHz. Surface and cross-sectional morphologies of the Si-LP electrodes after cycling were observed by a scanning electron microscope (SEM) without air exposure. Cyclability of the Si-LP electrodes in the electrolyte with and without FEC is shown in Fig. 1(a). Capacity retention for Si-LP electrode was substantially improved by the FEC-addition, although the discharge capacity at the 100th cycle decreased to 50% of the initial discharge capacity for the Si-LP electrode without FEC. To understand effects of the FEC-addition, EIS measurements were conducted and the SEI resistance ( R SEI ) was derived from the impedance spectra obtained at 0.1 V in the charging process. The SEI resistance for the Si-LP without FEC increased with increase in cycle number as shown in Fig. 1(b). By the FEC-addition, the SEI resistance was decreased and its increment with cycle number was substantially suppressed in comparison with the case of additive-free, indicating that reductive decomposition of the electrolyte on the Si-LP electrode was suppressed with a stable SEI film derived from FEC. Cross-sectional SEM images of the Si-LP electrodes after 10 and 30 cycles in the additive-free electrolyte are shown in Fig 1(c) and (d). Deposits of reductive products of the electrolyte were confirmed on Si-LPs. The amount of the deposition increased with cycle number, indicating a continuous decomposition of the electrolyte and a growth of SEI layer. The growth of the SEI layer lades an increment of the SEI resistance. Moreover, we found that the thickness of the Si-LP composite electrode was increased drastically by the growth of SEI layer and bending of Si-LPs, leading to a loss of the electric contact between the Si-LPs. Although Si-LPs bended after cycling, pulverization of Si-LPs was not observed. On the other hand, thinner SEI layer was observed on Si-LPs with the FEC-addition, and the expansion of the composite electrodes was suppressed. The stable SEI layer suppresses increment of the SEI resistance. Ensuring the electric-conducting path between active materials by the stable SEI layer is necessary to achieve a superior cycle performance of Si anodes. Acknowledgments : This work was supported by JST-ALCA-SPRING and JSPS-KAKENHI Grant Number 25820335 and 16H04649. References : [1] M. Saito et al ., J. Power Sources, 196, 6637 (2011).; [2] M. Haruta et al ., Electrochemistry, 83, 837 (2015). Figure 1
    Type of Medium: Online Resource
    ISSN: 2151-2043
    Language: Unknown
    Publisher: The Electrochemical Society
    Publication Date: 2016
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  • 7
    In: ECS Transactions, The Electrochemical Society, Vol. 16, No. 49 ( 2009-08-29), p. 469-477
    Abstract: The current efficiency for NF3 formation was investigated using Boron-Doped Diamond (BDD) anode in NH4F·nHF melts. It depended on both the current density and the NH4F-concentration. The best current efficiency was obtained at 40 mA/cm2 and the NH4F-concentration of 33.3 mol% (the NH4F·2HF melt), and its value was 72.4%.
    Type of Medium: Online Resource
    ISSN: 1938-5862 , 1938-6737
    Language: Unknown
    Publisher: The Electrochemical Society
    Publication Date: 2009
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  • 8
    Online Resource
    Online Resource
    The Electrochemical Society ; 2018
    In:  Journal of The Electrochemical Society Vol. 165, No. 9 ( 2018), p. A1874-A1879
    In: Journal of The Electrochemical Society, The Electrochemical Society, Vol. 165, No. 9 ( 2018), p. A1874-A1879
    Type of Medium: Online Resource
    ISSN: 0013-4651 , 1945-7111
    RVK:
    Language: English
    Publisher: The Electrochemical Society
    Publication Date: 2018
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  • 9
    Online Resource
    Online Resource
    The Electrochemical Society ; 2012
    In:  Journal of The Electrochemical Society Vol. 159, No. 10 ( 2012), p. A1630-A1635
    In: Journal of The Electrochemical Society, The Electrochemical Society, Vol. 159, No. 10 ( 2012), p. A1630-A1635
    Type of Medium: Online Resource
    ISSN: 0013-4651 , 1945-7111
    RVK:
    Language: English
    Publisher: The Electrochemical Society
    Publication Date: 2012
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  • 10
    Online Resource
    Online Resource
    The Electrochemical Society ; 2016
    In:  ECS Meeting Abstracts Vol. MA2016-03, No. 2 ( 2016-06-10), p. 955-955
    In: ECS Meeting Abstracts, The Electrochemical Society, Vol. MA2016-03, No. 2 ( 2016-06-10), p. 955-955
    Abstract: We had reported that am amorphous silicon flake powder (Si LeafPowder®, Si-LP), of which the lateral dimension and the thickness were ~4 μm and 100 nm, respectively, demonstrated superior cycle performances. [1, 2] Cyclability of the Si-LP electrodes was successfully improved by an addition of solid electrolyte interface (SEI)-forming additives such as vinylene carbonate (VC) and fluoroethylene carbonate (FEC). However, the capacity fading mechanism of the Si-LP electrodes has not been clarified. In order to understand the capacity fading of the Si-LP, variations of impedance components and the surface morphology associated with a decomposition of the electrolytes were investigated. Test electrodes were composed of Si-LP (83.3 wt.%), Ketjen Black (5.6 wt.%) and carboxymethyl cellulose sodium salt (11.1 wt.%), and coated on a Cu foil. The loading of the Si-LP composite was approximately 0.4 mg cm -2 . Electrolytes were 1 M LiPF 6 dissolved in a mixture of ethylene carbonate and diethyl carbonate (EC+DEC, 1:1 by vol.) with and without additive of 10 wt.% VC or FEC. Charge and discharge tests were conducted at C/2 rate in the CC-CV mode between 1.5 and 0.02 V using a two-electrode coin-type cell. The electrochemical impedance spectroscopy (EIS) was performed using a three-electrode cell in which impedance spectra were obtained by applying an AC voltage of 10 mV over the frequency range of 0.03 Hz to 300 kHz. Surface and cross-sectional morphologies of the Si-LP electrodes after cycling were observed by a scanning electron microscope (SEM) without air exposure. Cyclability of the Si-LP electrodes is shown in Fig. 1(a). Capacity retention for Si-LP electrodes was substantially improved by the VC- and FEC-addition, although the discharge capacity at the 100th cycle decreased to 50% of the initial discharge capacity for the Si-LP electrode in the additive-free electrolyte. To understand effects of VC- and FEC-addition, EIS measurements were conducted. Impedance components of the SEI layer, the electronic contact and the charge transfer were derived from the impedance spectra obtained at 0.1 V in the charging process. The SEI resistance of the Si-LP in the additive-free electrolyte increased with increasing cycle number as shown in Fig. 1(b), and the contact resistance also increased. The increments of the SEI and contact resistances with cycle number were suppressed by the VC- and FEC-addition. A thick SEI layer, originated from a continuous decomposition of the electrolyte, was observed by SEM on the Si-LP cycled in the additive-free electrolyte. Furthermore, we found that the thickness of the Si-LP composite was increased drastically by the growth of SEI layer, leading to a loss of the electronic contact between the Si-LPs. On the other hand, thinner SEI layers were observed on the Si-LPs cycled in the VC- and FEC-added electrolytes, and the expansion of the electrodes was suppressed. The continuous decomposition of the electrolyte was prevented by the stable SEI layer formed from decomposition products of VC and FEC, and therefore the increments of the SEI and contact resistances with cycle were suppressed. Ensuring the electronic-conducting path between active materials by the stable SEI layer is necessary to achieve a superior cycle performance of Si anodes. Acknowledgments : This work was supported by JST-ALCA-SPRING and JSPS-KAKENHI Grant Number 25820335. References : [1] M. Saito et al ., J. Power Sources, 196, 6637 (2011).; [2] M. Haruta et al ., Electrochemistry, 83, 837 (2015). Figure 1
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    ISSN: 2151-2043
    Language: Unknown
    Publisher: The Electrochemical Society
    Publication Date: 2016
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