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Enhancement of Columbic Efficiency and Capacity of Li-Ion Batteries using a Boron Nitride Nanotubes-Dispersed-Electrolyte with High Ionic Conductivity
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Enhancement of Columbic Efficiency and Capacity of Li-Ion Batteries using a Boron Nitride Nanotubes-Dispersed-Electrolyte with High Ionic Conductivity
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  • Dolly Yadav
    Dolly Yadav
    R&D Center, NAiEEL Technology, 6-2 Yuseongdaero 1205, Daejeon 34104, Republic of Korea
    More by Dolly Yadav
  • Jung-Hwan Jung
    Jung-Hwan Jung
    R&D Center, NAiEEL Technology, 6-2 Yuseongdaero 1205, Daejeon 34104, Republic of Korea
  • Yurim Lee
    Yurim Lee
    Department of Polymer Science and Engineering, Chungnam National University, Daejeon 34134, Republic of Korea
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  • Thomas You-Seok Kim
    Thomas You-Seok Kim
    R&D Center, NAiEEL Technology, 6-2 Yuseongdaero 1205, Daejeon 34104, Republic of Korea
  • Eunkwang Park
    Eunkwang Park
    R&D Center, NAiEEL Technology, 6-2 Yuseongdaero 1205, Daejeon 34104, Republic of Korea
  • Ki-In Choi
    Ki-In Choi
    R&D Center, NAiEEL Technology, 6-2 Yuseongdaero 1205, Daejeon 34104, Republic of Korea
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  • Jungho Cha
    Jungho Cha
    R&D Center, NAiEEL Technology, 6-2 Yuseongdaero 1205, Daejeon 34104, Republic of Korea
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  • Woo-Jin Song*
    Woo-Jin Song
    Department of Polymer Science and Engineering, Chungnam National University, Daejeon 34134, Republic of Korea
    Department of Chemical Engineering and Applied Chemistry, Chungnam National University, Daejeon 34134, Republic of Korea
    *Email: [email protected]
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  • Jae-Hak Choi
    Jae-Hak Choi
    Department of Polymer Science and Engineering, Chungnam National University, Daejeon 34134, Republic of Korea
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  • Seokgwang Doo
    Seokgwang Doo
    Department of Energy Engineering, Korea Institute of Energy Technology, 72 Unjeong-ro, Naju, Jeonnam 58217, Republic of Korea
  • Jaewoo Kim*
    Jaewoo Kim
    R&D Center, NAiEEL Technology, 6-2 Yuseongdaero 1205, Daejeon 34104, Republic of Korea
    *Email: [email protected]
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ACS Materials Letters

Cite this: ACS Materials Lett. 2023, 5, 10, 2648–2655
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https://doi.org/10.1021/acsmaterialslett.3c00538
Published August 30, 2023

Copyright © 2023 The Authors. Published by American Chemical Society. This publication is licensed under

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Abstract

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Carbon nanotubes (CNT) are currently used as conductive additives for the electrodes to enhance the capacity of the lithium-ion batteries (LIBs), and we herein for the first time demonstrate the feasibility of boron nitride nanotubes (BNNT) as an electrolyte additive for lithium ion batteries (LIBs). The 0.9 wt % BNNT electrolyte yielded enhanced Li-ion conductivity up to 30% (∼0.87 mS/cm) and a much higher Li-ion transference number (∼0.73) compared to electrolytes without BNNT. The BNNT dispersed electrolyte (1 M LiPF6 in ethylene carbonate/dimethyl carbonate) prepared via sonication serves as a new electrolyte formulation, together with the NCM622//graphite full cell, and exhibits the highest reversible capacities of 153 mAh/g at 1 C and excellent cyclic retention over 500 cycles at high 10 C with a specific capacity of 71.5 mAh/g and a Coulombic efficiency of 99.6% compared to 125.3 mAh/g at 1 C and 40 mAh/g at 10 C with only 97.5% Coulombic efficiency without BNNT, respectively. Overall, we suggest BNNT as a new class of functional electrolyte material that resolves the major limitations of conventional carbonate-based electrolytes and is compatible for different electrolytes/electrode materials aimed at practical implementations for current as well as advanced LIBs.

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Copyright © 2023 The Authors. Published by American Chemical Society

Over the last three decades, the materials technology and the manufacturing processes for LIBs have witnessed considerable advancement leading to improved capacities and rendering them capable of powering electric vehicles (EVs). (1−3) In the ongoing pursuit of increasing the energy densities and cycle retention of LIBs, a wide range of promising electrode materials have been tested and commercialized. (4−6) In this regard, carbon nanotubes became a crucial additive for the thick film electrodes increasing the capacity of the LIBs; however, its conductive nature restricted its application as an additive to the separators and/or electrolytes. The electrolytes play an essential role in determining the electrochemical performance of the LIBs. Arguably, one of the biggest challenges is the choice of a suitable electrolyte solution with good ionic conductivity, high Li ion transference, and wide electrochemical stability. The nature of the electrolyte plays a more important role in conventional Li-ion batteries, in determining the nature of solid electrolyte interphase (SEI) formation and regulation of the mass transport of Li+ during the cycling process. Lithium stripping/plating, dendrite growth, effective passivation by SEI, and interference by side reactions are all influenced by the nature of the electrolyte. However, the availability of free Li+ and the medium for transport during the cycling process is a major manipulator that regulates the capacity of the LIBs.

Despite considerable progress made in solid-state electrolytes (SSE) and ionic liquids (IL), conventional liquid electrolytes are still considered the most commonly used electrolytes for LIBs. (7−11) However, due to some inherent limitations, they suffer from long-lasting detrimental loss of capacity of the LIBs. (12,13) In this regard, the electrolyte formulation strategy comes into play, where different additives are added to the conventional electrolytes in order to improve the battery performance. (14−18) Commonly, the electrolyte additives usually comprise of functional molecules that are preferentially involved in the interfacial redox process thereby prior to the electrolytes. (15) They not only improve the interfacial SEI formation but also determine the ionic conductivity and stability of the electrolytes. However, other issues like the reduction in the irreversible capacity, gas generation, thermal stability of Li salt (LiPF6) against organic solvents, and protection of cathode from dissolution and overcharging yet need to be addressed. (17,18) Since not all the desired functions can be achieved by one single additive, hence, binary and ternary additives systems were proposed which definitely adds to the cost and feasibility of the system. (19)

The boron-based additives have been a topic of interest for LIBs. (20,21) Inspired by the promising applications of the hexagonal boron nitrides (h-BN), (22,23) boron nitride nanotubes (BNNT) have been attracted as a viable advanced multifunctional material. (24−26) To date, BNNT has been explored as a protective coating to the separators to reduce the cell short circuit, enhance thermal stability and Li+ conductivity. (25,27) The arrangement of BNNT on the separator results in enhanced Li+ transport, producing a high capacity and negligible change in electrical resistivity. However, incorporating BNNT as an additive into a conventional electrolyte has not been explored. BNNT as an additive would essentially benefit electrolytes with higher ionic conductivity, resulting in boosted Li+ transportation along with resolving thermal issues in LIBs. The fact that the boron centers in BNNT are electron deficient (Lewis acid), they may interact with the oxygen rich electrolyte molecules leading to desolvation of Li+ and hence, improving lithium ion transport through the surface of BNNT as well as inside the tubes. (27)

In this regard, we herein demonstrated, for the first time, the feasibility of BNNT as a multifunctional electrolyte additive to enhance the performance of the conventional LIBs (Scheme 1). BNNT used for the current study displays an open-ended and need-like morphology with a relatively small aspect ratio of 200∼300. (28,29) The SEM image (Figure S1a, Supporting Information) displays the presence of cylindrical nanotube-like morphology with an average length of 5–10 μm. The TEM image of the BNNT (Figure S1b, Supporting Information) displays open-ended cylindrical hollow structures with an outer diameter of 30–50 nm and a length of 5–10 μm in average. The schematic illustration of BNNT dispersion in a 1 M LiPF6 EC/DMC based conventional electrolyte (BNNT-electrolyte) through simple sonication is shown in Scheme 1a. The dispersion of BNNT into electrolytes enhances the confinement effect of the anions at the defect sites. (23−25) In contrast to the conventional electrolytes, Li+ are strongly coordinated with the solvent molecules resulting in comparatively lower capacity and cycle stability also, the Lewis acid interaction between the anions/solvent and the BNNT may facilitate the dissociation of Li+ and accelerate Li+ transport leading to high Li+ transference number. (20) The structural advantage of BNNT for ion transport in fluid media can also be deduced by its hollow and cylindrical geometry (Figure S1b, Supporting Information) that allows fast movement of ions at the surface as well as inside the nanotubes under osmotic, electric, chemical forcing, and their combinations. (26) The Fourier-transform infrared spectroscopy (FTIR, Figure S2, Supporting Information) for the calcinated BNNT (850 °C) conferred the presence of the −OH functional group (3216 cm–1). The −OH functional groups on the BNNT surface serve as interaction sites for the Li-ions providing a channelized pathway for the Li-ion transference during the charge/discharge cycles. (30,31) Hence, BNNT would serve as an excellent electrolyte additive to conventional carbonate electrolytes, bringing multifunctional advantages to LIBs.

Scheme 1

Scheme 1. Design of a BNNT Dispersed Electrolyte, (a) Dispersion of BNNT in Electrolyte through Simple Sonication, and (b) Schematic of NCM/Separator/Graphite Full Cell with BNNT-Dispersed Electrolyte

The ionic conductivities of BNNT-dispersed electrolytes were measured by electrochemical impedance spectroscopy (EIS), using identical standard stainless-steel disks blocking electrodes at temperatures ranging from −10, 25, and 60 °C, respectively. As shown in Figure 1a, the room temperature ionic conductivities of different BNNT concentrations in 1 M LiPF6 EC/DMC exhibit an upward trend of 0.61, 0.77, 0.80, 0.87, and 0.84 mS/cm with 0.0, 0.5, 0.7, 0.9, and 1.1 wt % of BNNT, respectively. The ionic conductivity of an electrolyte depends on the population of dissociated ion pairs. The Lewis acid sites in the BNNT are assumed to interact with the oxygen of the cyclic carbonates leading to the desolvation of Li+. Hence, the higher ionic conductivity with BNNT could be due to the enhanced movement of free Li+ at the surface and inside the nanotubes and the reduced mobility of the competing anions absorbed at the defect sites in BNNT. Such a phenomenon can be interpreted by the elevated transport channels introduced by BNNT in various transport applications. In addition, the deterioration of LIBs could be minimized with the BNNT electrolytes in terms of ionic conductivity stability with time (Figure 1a). The 0.9 wt % BNNT electrolyte exhibits an improved ionic conductivity of 0.27 mS/cm at −10 °C, which is ∼23% higher than the neat electrolyte (0.22 mS/cm). As expected, BNNT also presents stable and higher ionic conductivity at a high temperature of 60 °C, hence supporting excellent temperature endurance and high Li+ transportation for the BNNT-dispersed-electrolyte (Figure 1b). Comparably, the ionic conductivity for 0.9 wt % BNNT electrolyte is the best among other functional additives dispersed electrolytes prepared and measured under the same conditions and environments (Figure S3, Supporting Information).

Figure 1

Figure 1. (a) Ionic conductivity of x wt % BNNT in 1 M LiPF6 in EC/DMC (1:1 v/v), where x = 0, 0.5, 0.7, 0.9, and 1.1 wt % at 25 °C. (b) Temperature dependent ionic conductivity of the neat and with 0.9 wt % BNNT.

The Li+ transport efficiency of BNNT electrolytes was also confirmed through their Li+ transference numbers. A symmetric Li (Li//Li) cells with different wt % of BNNT added electrolytes were prepared for measuring tLi+ using the potentiostatic polarization method. (24) The Nyquist plots for the neat and 0.9 wt % BNNT electrolyte are shown in Figure S4. The neat electrolyte displayed tLi+ of ∼0.49 which is in good accordance with the reported literature (tLi+ = 0.47 for 1 M LiPF6 in equivolume EC/DMC). (32) The tLi+ increases with an increase in the wt % of BNNT up to 0.73 for 0.9 wt % BNNT, followed by a further decrease in the tLi+ of 0.70 for 1.1 wt % BNNT (Table 1). Decrease of the tLi+ with higher wt % of BNNT could be partly due to lower amount of electrolyte with increased BNNT content for the equal amount of electrolyte and probable aggregation of BNNT as the concentration is increased in part. The remarkable transport efficiency could be attributed to the structural and surface properties of BNNT that assist the channelized pathway for boosted Li+ transportation imposed by confinement and complexation to the free anions (23) leading to preferential transport of Li+ through the surface and open hollow cylindrical structure.

Table 1. Parameters for the Determination of the Li+ Transference Number with Different wt% of BNNT
BNNT (wt %)R0 (Ω)I0 (μA)Iss (μA)Rss (Ω)tLi+
0 wt %380.4421.9019.30362.590.49
0.5 wt %254.6232.4030.10250.240.66
0.7 wt %221.3539.3037.70218.100.70
0.9 wt %224.2235.6034.00216.230.73
1.1 wt %259.7026.1623.40251.860.70

Further, the electrochemical stability window for BNNT-dispersed-electrolytes was evaluated by cyclic voltammetry (CV) using stainless-steel and Li metal as a working and counter/reference electrode, respectively. The CV curves of the cells using neat and 0.9 wt % BNNT electrolytes show reversible Li/Li+ stripping-plating behavior on steel electrodes between −0.5 and 5.0 V vs Li/Li+ (Figure S5, Supporting Information). The CV curves for 0.9 wt % BNNT added electrolyte (Figure S5a, Supporting Information) exhibited a stable behavior upon repeat cycle in comparison to the neat electrolyte (Figure S5b, Supporting Information). The irreversible moderate oxidation peaks beyond 4.8 V, for 0.9 wt % BNNT electrolyte, demonstrate the electrochemical stability of BNNT added electrolytes with a feasible working window for practical battery applications (inset, Figure S5a, Supporting Information). Indeed, the lower HOMO energy level of EC results in facile oxidation at the cathodic site presenting in lower capacity and lesser cycle stability. (33) However, when BNNT is incorporated into the conventional electrolytes, the boron sites in BNNT interact with the cyclic EC molecules, thereby lowering the chances of electrolyte oxidation, which in turn causes improved capacity and long cycle stability.

In order to experimentally provide the feasibility of practical full cells based on the above assumptions, Li-ion full cell using commercial NCM622 cathode and graphite anode was fabricated with 0.9 wt % BNNT electrolyte (Figure 2). The NCM622//graphite full cell was precycled at a voltage range of 2.7–4.2 V at 0.1 C (Figure 2a). The 0.9 wt % BNNT electrolyte displayed a higher charge capacity (160.3 mAh/g) than the neat electrolyte (152 mAh/g) at 0.1 C. Figure 2b-d shows the temperature dependent electrochemical rate performance of the NCM622//graphite full cell for neat and 0.9 wt % BNNT electrolytes. The rate performance was tested from 0.5C to 15C and back to 1C for neat and 0.9 wt % BNNT electrolyte at 25 °C (Figure 2b) and at 60 °C (Figure 2c). The rate performance at 0.5, 1.0, 5.0, 10, and 15 C for 0.9 wt % BNNT electrolyte at room temperature exhibited specific capacities of 157.9, 153.2, 137.2, 81.2, and 39.5 mAh/g respectively, while the neat electrolyte exhibits 129.4, 125.3, 91.0, 23.13, and 9.7 mAh/g, respectively (Figure 2b). The BNNT electrolytes also exhibited stable and enhanced rate performance at 60 °C with a specific capacity of 116.4, 108.4, 87.99, 65.91, and 40.82 mAh/g, while the neat electrolyte showed lower capacities of 83.9, 71.69, 50.25, 31.13, and 15.5 mAh/g at 0.5, 1.0, 5.0, 10, and 15 C, respectively (Figure 2c).

Figure 2

Figure 2. (a) Precycle voltage profile for NCM622//graphite full cell at 0.1 C, where 1 C = 1.02 mA/cm2 with voltage window of 4.2–2.7 V for Neat and 0.9 wt % BNNT electrolyte, (b) rate performance of NCM//graphite full cell at 25 °C from 0.5 to 15 C for 10 cycles, (c) at 60 °C from 0.5 to 15 C for 5 cycles, (d) at −10 °C from 0.5 to 10 C for five cycles, and (e) galvanostatic cycling of NCM//graphite full cell at 10 C for 500 cycles at 25 °C.

More importantly, the BNNT electrolyte exhibits a stable rate performance at a freezing temperature of −10 °C (Figure 2d). The 0.9 wt % BNNT electrolyte exhibited 88.6, 38.7, 4.9, and 0.95 mAh/g, while the neat electrolyte exhibited 63.3, 27.1, 4.7, and 0.04 mAh/g at 0.5, 1.0, 5.0, and 10 C, respectively. Further, the cells regained their capacity to 56.1 mAh/g for 0.9 wt % BNNT and 39.2 mAh/g for neat electrolyte at 0.5 C. The lower performance for neat electrolyte could be due to the freezing of the EC at low temperature causing an increase in the ionic resistivity and leading to a rise in the over potential thereby causing a lowering in the ionic conductivity. (34) Also, the low kinetics for Li+ transport induced slow diffusion of Li+ in the active medium that cannot be ignored. In addition, the 0.9 wt % BNNT electrolyte also showed good cycling retention at a high C-rate of 10 C with 71.5 mAh/g specific capacity for over 500 cycles with Coulombic efficiency of 99.6% at 25 °C, while the neat electrolyte showed comparatively lower capacity of 40 mAh/g with only 97.5% Coulombic efficiency under similar conditions (Figure 2e). Hence, it is quite evident that using BNNT as an additive to conventional electrolytes helps in increasing their capacity, cycle retention, varied temperature tolerance, and even stable performance at the higher C-rates.

The postcycle morphology of the electrodes and the separators were imaged by scanning electron microscopy (SEM), to evaluate the effect of BNNT dispersed electrolyte on the performance of the NCM622//graphite full cell. Figure 3 shows the SEM image of the cycled NCM622//graphite full cell at 10 C after 100 cycles. The cycled NCM622 cathode using a neat electrolyte shows little deformation on the surface (Figure 3a) in comparison to the fresh cathode (Figure S6a, Supporting Information). The cycled graphite anode (Figure 3b, 3c) also shows uneven and broken SEI layer formation. The cycled NCM622//graphite full cell using 0.9 wt % BNNT electrolyte shows the presence of BNNT on the NCM surface (Figure 3d, inset and in the cross-section 3e, 3f) along with well-maintained surface even after long cycling experiments (10 C for 100 cycles). Figure 3g–i shows the SEM image of the cycled graphite anode cycled using 0.9 wt % BNNT electrolyte with uniform SEI layer on its surface. The cross section of the anode (Figure 3h, i) also shows the formation of a uniform and porous SEI layer with BNNT deposited on the anode surface as well as embedded in the SEI layer. The presence of BNNT on the surface of the electrode materials is expected to increase the thermal stability of the electrolyte, improve the electrode/electrolyte interface, and the capacity of the LIB. Additionally, the presence of BNNT on the PP separator can also be seen on its surface which expects not only to increase the thermal stability of the separator (Figure S6c, Supporting Information) but also to enhance the ionic conductivity due to directionally oriented to the electrodes (Figure S6d, Supporting Information). The thermal shrinkage of the PP separator procured from the disassembled cells after the cycling experiment was conducted in a convection oven at 120 °C for 1 h. The PP separators with different wt % of BNNT exhibit apparently lesser shrinkage in comparison to the PP separator than that of the neat electrolyte (Figure S7, Supporting Information). As shown in Figure S7, the thermal shrinkage for the PP separator cycled in neat electrolyte was ∼10.5%, which was comparatively higher than the PP separators cycled in BNNT electrolytes with only 5.3, 5.3, 4.7, 4.2, and 2.6% thermal shrinkage for 0.5, 0.7, 0.9, 1.1, and 1.8 wt % BNNT, respectively. Consequently, the introduction of BNNT into conventional electrolytes can remarkably suppress the thermal shrinkage of the PP separator ensuring better battery safety at high temperatures in addition to the increase of the ionic conductivity.

Figure 3

Figure 3. SEM image of disassembled NMC//graphite full cell after 100 cycles at 10 C with neat electrolyte: (a) NCM622 cathode, (b) Graphite anode, (c) cross section of graphite anode, and using 0.9 wt % BNNT electrolyte; (d) NCM622 cathode (inset showing BNNT dispersed on NCM surface); (e, f) cross section of NCM cathode showing presence of BNNT; (g) surface of graphite anode revealing SEI formation; and (h, i) cross section of graphite anode showing the presence of BNNT embedded below the SEI layer. The yellow arrows show the presence of BNNT inside the SEI layer (BNNT attached on the anode surface when the cell first assembled, SEI layer formed during the cycle test).

For more practical assessment, the 0.9 wt % BNNT electrolyte along with the lithium metal anode and NCM622 cathode was also evaluated. The lithium metal has attracted much attention owing to its high specific capacity (3,860 mAh/g) and low mass density (0.59 g/cm3), however, suffers from poor cycle stability due to the formation of Li-dendrites leading to cell short circuit. (36) The galvanostatic cycling performance for NCM//Li half-cell (Figure S8, Supporting Information) cycled at 0.5 C with a voltage window of 2.7–4.0 V displayed a specific capacity of 175.0 mAh/g with ∼98.7% Coulombic efficiency for 25 cycles, while 153 mAh/g with ∼97.6% Coulombic efficiency for 25 cycles for the neat electrolyte. Furthermore, the LCO//Graphite pouch cells (3 × 3 cm2) for neat and 0.9 wt % BNNT electrolyte were fabricated and precycled at 0.1 C after aging for 36 h (Figure S9, Supporting Information). The precycled LCO//Graphite pouch was cycled at 0.5 C with a voltage window of 4.35 to 2.7 V and exhibited a stable capacity of 15.5 mAh/g retaining 97% Coulombic efficiency even after 300 cycles (Figure S10, Supporting Information). However, the neat electrolyte displayed continuous loss in capacity retaining ∼5.0 mAh/g after 300 cycles with 94.3% Coulombic efficiency at 0.5 C.

Our study strongly suggests that BNNT proves to be an excellent candidate as an electrolyte additive for current LIBs as well as various advanced secondary batteries, including hybrid and all solid-state batteries. Figures S11–S13 shows the X-ray photoelectron spectrometry (XPS) for BNNT before and after exposure to the electrolyte (details in the Supporting Information). After immersing BNNT in the electrolyte for 24 h, followed by centrifugation and vacuum-drying at 100 °C for 24 h, the dried BNNT was then investigated to determine the remaining electrolyte components on the BNNT’s surface. A comparative survey (Figure S11) and the core level spectra (Figure S13) for BNNT after electrolyte exposure displays the presence of F, O, C, N, B, P, and Li with binding energies of F 1s, O 1s, C 1s, N 1s, B 1s, P 2p, and Li 1s at 686.44, 532.71, 284.78, 397.87, 190.3, 134.35, and 55.51 eV, respectively, thereby conferring that the BNNT exhibits electrostatic interactions with the cations, anions as well as the oxygen-rich electrolyte molecules (Figures S11, S12a–g). (35) Further an increase in the carbon and oxygen contents for BNNT after exposure to the electrolyte supported the presence of the electrolyte residue on the BNNT surface. The presence of EC/DMC-related carbon components originates from C–C/C–H (284.78 eV) together with minor contributions from C–O (286.72 eV) and C═O (288.37 eV) species (Figure S13d), which could originate from solvent residues on the BNNT surface. (36) Also, an additional peak a 193.75 eV corresponding to Li–O–B species was also observed for BNNT after electrolyte exposure. (37,38)

The tentative mechanism for Li+ transport for 0.9 wt % BNNT electrolyte is depicted in Scheme 2. The B–N bonds in BNNT are significantly ionic in nature due to the local dipole moment, a typical phenomenon observed in two adjacent heteroatoms. (39,40) This endows BNNT favorable for the electrostatic interactions with the cations, (40) as well as the anions, (39) in the electrolyte thereby providing a pathway for facilitating the Li+ transport. The Lewis acid sites in the BNNT are assumed to interact with the oxygen of the cyclic carbonates, leading to the desolvation of Li+ and hence providing free Li+ responsible for enhanced Li-ion transport. Whereas, the defects sites in BNNT serve as binding sites for the anions, channelizing the transport of Li+ during the charge/discharge process. (20,40) Moreover, due to the structural advantage of the BNNT, (27−29,41) commonly investigated for ion transport in fluid media the open-end hollow cylindrical structure allows the exhohedral and endohedral transport of Li+ through electrostatic interactions. (42−47) Hence, due to the multiple structural benefits, BNNT qualifies as an excellent electrolyte additive for LIBs.

Scheme 2

Scheme 2. Schematic for of the Li+ Transport during Charge and Discharge in (a) Neat Electrolyte and (b) 0.9 wt % BNNT Electrolyte

In summary, this investigation demonstrates that BNNT dispersed in the conventional electrolytes promotes Li-ion transport efficiency by hindering anion mobility and facilitating Li-ion conduction. Resulting in ∼30% higher ionic conductivity and ∼48% higher tLi+ value than those for the neat electrolyte could offers alleviated polarization, stabilized electrolyte-electrode interfaces, and extended cycle lifespan for current LIBs as well as advanced battery systems. Good capacity retention at a high C-rate (10 C) over 500 cycles while enhancing thermal stability offers the feasibility of BNNT based electrolytes for the high energy density LIBs. Notably, the stable capacity performance at varied temperature conditions (−10 to 60 °C) also offers a solution to the deterioration of LIBs under freezing as well as high temperature conditions, proving its multifunctionality and versatility for future high-performance LIBs. The BNNT electrolytes also show stable and enhanced electrochemical cycle performance for varied cathode (NCM622, LCO) and anode materials (graphite, lithium metal) emphasizing its compatibility with different secondary storage devices. Overall, the above findings further highlight previously unrecognized advantages of BNNT as an electrolyte additive, addressing the major limitations of the conventional carbonate-based electrolyte systems and can provide practical beneficial implementations for the current as well as the advanced battery systems.

Supporting Information

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The Supporting Information is available free of charge at https://pubs.acs.org/doi/10.1021/acsmaterialslett.3c00538.

  • Experimental details, ionic conductivities of different filler materials, EIS, CV, SEM images, thermal stability of PP separator, cycle performance of NCM/Li half-cell, voltage profiles and cycle performance of LCO//Graphite pouch cell, and XPS spectra of BNNT before and after electrolyte exposure (PDF)

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Author Information

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  • Corresponding Authors
    • Woo-Jin Song - Department of Polymer Science and Engineering, Chungnam National University, Daejeon 34134, Republic of KoreaDepartment of Chemical Engineering and Applied Chemistry, Chungnam National University, Daejeon 34134, Republic of Korea Email: [email protected]
    • Jaewoo Kim - R&D Center, NAiEEL Technology, 6-2 Yuseongdaero 1205, Daejeon 34104, Republic of KoreaOrcidhttps://orcid.org/0000-0003-3472-0180 Email: [email protected]
  • Authors
    • Dolly Yadav - R&D Center, NAiEEL Technology, 6-2 Yuseongdaero 1205, Daejeon 34104, Republic of KoreaOrcidhttps://orcid.org/0000-0003-1322-8074
    • Jung-Hwan Jung - R&D Center, NAiEEL Technology, 6-2 Yuseongdaero 1205, Daejeon 34104, Republic of KoreaOrcidhttps://orcid.org/0000-0002-3352-1940
    • Yurim Lee - Department of Polymer Science and Engineering, Chungnam National University, Daejeon 34134, Republic of Korea
    • Thomas You-Seok Kim - R&D Center, NAiEEL Technology, 6-2 Yuseongdaero 1205, Daejeon 34104, Republic of KoreaOrcidhttps://orcid.org/0009-0006-9392-8431
    • Eunkwang Park - R&D Center, NAiEEL Technology, 6-2 Yuseongdaero 1205, Daejeon 34104, Republic of Korea
    • Ki-In Choi - R&D Center, NAiEEL Technology, 6-2 Yuseongdaero 1205, Daejeon 34104, Republic of Korea
    • Jungho Cha - R&D Center, NAiEEL Technology, 6-2 Yuseongdaero 1205, Daejeon 34104, Republic of Korea
    • Jae-Hak Choi - Department of Polymer Science and Engineering, Chungnam National University, Daejeon 34134, Republic of KoreaOrcidhttps://orcid.org/0000-0002-7101-646X
    • Seokgwang Doo - Department of Energy Engineering, Korea Institute of Energy Technology, 72 Unjeong-ro, Naju, Jeonnam 58217, Republic of Korea
  • Author Contributions

    D.Y. (Dolly Yadav), J.-H.J. (Jung-Hwan Jung), and Y.L. (Yurim Lee) contributed equally to this study. CRediT: Jaewoo Kim conceptualization, funding acquisition, investigation, project administration, writing-review & editing.

  • Notes
    The authors declare no competing financial interest.

Acknowledgments

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This work was financially supported by the R&D Projects Grant No. S3258477 sponsored by the Ministry of SMEs and Startups and Grant No. 20017989 (ATC+ Program) sponsored by the Ministry of Trade, Industry and Energy of Republic of Korea.

References

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  1. Numan Yanar, Thomas You-Seok Kim, Junghwan Jung, Duy Khoe Dinh, Ki-in Choi, Arni G. Pornea, Dolly Yadav, Zahid Hanif, Eunkwang Park, Jaewoo Kim. Boron Nitride Nanotube-Aligned Electrospun PVDF Nanofiber-Based Composite Films Applicable to Wearable Piezoelectric Sensors. ACS Applied Nano Materials 2024, 7 (10) , 11715-11726. https://doi.org/10.1021/acsanm.4c01296
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  • Abstract

    Scheme 1

    Scheme 1. Design of a BNNT Dispersed Electrolyte, (a) Dispersion of BNNT in Electrolyte through Simple Sonication, and (b) Schematic of NCM/Separator/Graphite Full Cell with BNNT-Dispersed Electrolyte

    Figure 1

    Figure 1. (a) Ionic conductivity of x wt % BNNT in 1 M LiPF6 in EC/DMC (1:1 v/v), where x = 0, 0.5, 0.7, 0.9, and 1.1 wt % at 25 °C. (b) Temperature dependent ionic conductivity of the neat and with 0.9 wt % BNNT.

    Figure 2

    Figure 2. (a) Precycle voltage profile for NCM622//graphite full cell at 0.1 C, where 1 C = 1.02 mA/cm2 with voltage window of 4.2–2.7 V for Neat and 0.9 wt % BNNT electrolyte, (b) rate performance of NCM//graphite full cell at 25 °C from 0.5 to 15 C for 10 cycles, (c) at 60 °C from 0.5 to 15 C for 5 cycles, (d) at −10 °C from 0.5 to 10 C for five cycles, and (e) galvanostatic cycling of NCM//graphite full cell at 10 C for 500 cycles at 25 °C.

    Figure 3

    Figure 3. SEM image of disassembled NMC//graphite full cell after 100 cycles at 10 C with neat electrolyte: (a) NCM622 cathode, (b) Graphite anode, (c) cross section of graphite anode, and using 0.9 wt % BNNT electrolyte; (d) NCM622 cathode (inset showing BNNT dispersed on NCM surface); (e, f) cross section of NCM cathode showing presence of BNNT; (g) surface of graphite anode revealing SEI formation; and (h, i) cross section of graphite anode showing the presence of BNNT embedded below the SEI layer. The yellow arrows show the presence of BNNT inside the SEI layer (BNNT attached on the anode surface when the cell first assembled, SEI layer formed during the cycle test).

    Scheme 2

    Scheme 2. Schematic for of the Li+ Transport during Charge and Discharge in (a) Neat Electrolyte and (b) 0.9 wt % BNNT Electrolyte
  • References


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  • Supporting Information

    Supporting Information


    The Supporting Information is available free of charge at https://pubs.acs.org/doi/10.1021/acsmaterialslett.3c00538.

    • Experimental details, ionic conductivities of different filler materials, EIS, CV, SEM images, thermal stability of PP separator, cycle performance of NCM/Li half-cell, voltage profiles and cycle performance of LCO//Graphite pouch cell, and XPS spectra of BNNT before and after electrolyte exposure (PDF)


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