Rational design of Ru/TiO2/CNTs as cathode: promotion of cycling performance for aprotic lithium-oxygen battery
Abstract
Realizing long-life cycling is the biggest challenge in the research field of Li-O2 batteries in the current stage. The main reasons for poor cycling performance are the sluggish Li2O2 formation and decomposition process, as well as the side reaction of carbon cathode. In order to accurately address the problems above, a TiO2/CNTs cathode was rationally designed for long-life Li-O2 batteries. The CNTs skeleton offers multiple three-dimensional channels for the rapid transportation of oxygen, Li+ and electrons. A thin-film and discontinuous layer of TiO2 is coated on the CNTs surface to effectively inhibit the carbon corrosion but still could let mass transfer smoothly. Ultrafine Ru nanoparticles decorating the TiO2/CNTs serve as efficient catalytic active sites. Benefiting from the unique structure design, Li-O2 batteries with the cathode of TiO2/CNTs achieve a cycling life of 110 with a fixed capacity of 500 mAh g-1 at a current density of 100 mA g-1. Our research generates new ideas for designing long-cycling Li-O2 battery cathodes.
Keywords
INTRODUCTION
Li-ion batteries are approaching their theoretical limit in energy density, although they have truly changed the world by serving as either portable or large-scale energy storage system[1]. Nonaqueous lithium-oxygen (Li-O2) battery, an emerging next-generation energy storage system, shows an extremely high theoretical energy density that is almost several times that of state-of-the-art Li-ion batteries[2]. The electrochemistry of a nonaqueous Li-O2 battery is simply based on the reaction between oxygen and Li on a porous cathode[3-6]. Nevertheless, such a simple reaction conceals quite complicated aspects which affect the final performance of a Li-O2 battery. With a certain electrolyte, the cathode and its structure and type of catalyst largely govern the formation route and the structure and morphology of the Li2O2, which in turn influences the capacity, overpotential and lifespan of Li-O2 batteries.
So far, two main types of Li2O2 formation route have been studied and the intrinsic relationships of their structure and the electrochemical behaviors have been widely accepted by researchers[3,4,7-11]. The Li-O2 battery with toroidal-structured Li2O2 usually delivers a high discharge capacity because of its large size, which of course leads to a large charge overpotential to decompose. Film-or shape-structured Li2O2 are rather easier to decompose during charging process, but the cathode surface will be fully passivated once such a thin film is formed and the discharge process will be terminated, leading to a low capacity. As we all expect, large discharge capacity and low charge overpotential is the ultimate goal of developing Li-O2 battery, which implies that the ideal Li2O2 should have premium size, crystalline and in particular the cathode surface should still feature a porous structure after being generated[9,12-14]. Therefore, a variety of strategies to regulate the Li2O2 formation have been proposed, including rational cathode design, surface engineering, multicomponent catalyst employment, and so on[15-19]. With these measures in hand, in recent years, Li2O2 with different favorable morphologies have been discovered, which helped decrease the overpotential and enlarge the capacity to some extent. However, the cycling performance is still far from satisfactory and needs more attention[15-17]. As we all know, carbon materials show their overwhelming advantage in serving cathode in Li-O2 batteries due to their low price and excellent electron conductivity[20,21], but carbon corrosion upon battery cycling is an unavoidable factor that leads to battery failure[22-24]. Therefore, designing a cathode that could regulate favorable Li2O2 formation/ decomposition and meanwhile could retain the merit of carbon materials while avoiding the side reactions will be of high significance to building long-life Li-O2 batteries[25,26].
Herein in this work, a rational design of TiO2/CNTs cathode is presented. A thin and loose TiO2 layer partially coats the CNTs surface, followed by decorating ultrafine Ru nanoparticles on the TiO2/CNTs. Several advantages can be revealed in this cathode design: (i) The CNTs skeleton offers multiple three-dimensional channels for the rapid transportation of oxygen, Li+ and electrons; (ii) The large surface area provides huge space for Li2O2 accommodation; (iii) The thin-loose TiO2 layer effectively inhibits the carbon corrosion but still could let mass transfer; and (iv) The ultrafine Ru nanoparticles serves as catalytic active sites. Taking these four aspects above in consideration, a long-life Li-O2 battery is constructed.
EXPERIMENTAL
Preparation of the catalyst
A certain amount of the commercial multiwall carbon nanotubes (MWCNTs) was firstly oxidized with a solution (200 mL) that contained 75 mL nitric acid (65%-68%) and purified water under vigorous stirring overnight to remove impurities. Then it was washed with deionized water and ethanol several times, followed by drying at 80 °C in air.
TiO2/CNTs was achieved by the hydrolysis of the titanium butoxide on the surface of CNTs, and the method was modified by a previous report[27]. Ru nanoparticles were then loaded on the TiO2/CNTs via a modified aqueous reduction route[28]. In detail, in a flask (250 mL), a certain amount of RuCl3·3H2O was dissolved in 100 mL aqueous solution and then 100 mg of TiO2/CNTs was added to form a mixture. This mixture was stirred for 24 h at room temperature. Afterwards, 10 mL aqueous solution of NaBH4 was added dropwise to the previous solution to keep the molar ratio at 3 by controlling the volume of NaBH4 and the weight of RuCl3·3H2O. The Ru/TiO2/CNTs black powder was generated after 1 h vigorous stirring. Then, the resulting solid product was washed with water and ethanol via centrifugation several times and finally dried in a vacuum oven at 80 °C overnight.
Physical characterizations
X-ray diffraction (XRD) (GBC mini materials analyser MMA) patterns were performed at a scan rate of
Li-O2 battery measurements
For the fabrication of the cathode, catalyst (80 wt.%), Ketjen Black (KB10 wt.%), and poly(1,1,2,2-tetrafluoroethylene) (PTFE) (60% dispersion, 10 wt.%) were mixed in an isopropanol solution to get a homogeneous slurry, which was then coated on carbon paper. Afterwards, the electrodes were dried in a vacuum oven at 120 °C overnight. All the lithium-oxygen batteries were assembled in an Ar-filled glove box (Mbraun, Unilab, Germany) with both water and oxygen contents below 0.1 ppm. 2032-type coin cells with 9 air holes on the cathode cape were employed as Li-O2 batteries. Apart from cathode, in a typical Li-O2 battery, lithium metal acted as the counter electrode while 1 M LiCF3SO3 dissolved in tetraethylene glycol dimethyl ether (TEGDME) worked as electrolyte. All the assembled coin cells were stored in an O2-purged homemade chamber which was connected to the battery tester (LAND CT 2001) for 2 h before each test. The galvanostatic discharge-charge tests were then conducted in the potential range of 2.0-4.5 V (vs. Li+/Li). The loading amount in each cathode was about 0.6~0.8 mg cm-2.
Examination of the discharged and recharged electrodes was realized by disassembling the batteries in the glove box, followed by rinsing the cycled electrode with tetraethylene glycol dimethyl ether (TEGDME) and removing the solvent under vacuum. For ex-situ SEM and XPS measurements, the collected electrodes were put in a plastic package and laminated in the glove box before taking them out to the outside instruments.
RESULTS AND DISCUSSION
Structure and morphology analysis
The fabrication process of the Ru/TiO2/CNTs cathode consisted of two steps [Figure 1]. TiO2/CNTs was firstly prepared by the hydrolysis of the titanium butoxide on the surface of CNTs. Ultrafine Ru nanoparticles were then loaded on TiO2/CNTs via an aqueous reduction reaction. The rational designed Ru/TiO2/CNTs cathode was anticipated to effectively catalyze the reversible Li2O2 formation and decomposition.
Figure 1. Schematic illustration of the preparation route of Ru/TiO2/CNTs.
The CNTs had a diameter of 15 nm and showed a very distinct layered structure of nano-walls [Figure 2A]. Both light and dart fields were utilized to well characterize the microstructure of Ru/CNTs and Ru/TiO2/CNTs. Ultrafine Ru nanoparticles with a size of 2-3 nm were decorated on the surface of CNTs in the sample of Ru/CNTs [Figure 2B and C]. The existence of TiO2 in the sample of Ru/TiO2/CNTs nanocomposites could be evidenced by the typical interplanar spacings of 0.35 nm, which was well consistent with the d-spacing of the (101) crystal planes of rutile TiO2 (JCPDS 21-1272) [Figure 2D and E]. Meanwhile, Ru nanoparticles could also be found deposited on the surface of TiO2, which could be further evidenced by HR-TEM element mapping [Supplementary Figure 1]. The indexed diffraction rings in the selected area electron diffraction (SAED) pattern also verified the rutile structure of TiO2 [Figure 2F] . The EDS spectrum of the Ru/TiO2/CNTs also verified the material constitution, and showed that the loading amount of Ti and Ru was 3.1% and 43.3% (atom weight percentage) [Figure 2G and H]. The specific surface area of the Ru/TiO2/CNTs is 968.3 m2/g.
Figure 2. Physical characterizations. (A) TEM images of CNTs, HRTEM image of Ru/CNTs (B) dark field and (C) light field, HRTEM image of Ru/TiO2/CNTs (D) dark field and (E) light field; (F) SAED pattern of Ru/TiO2/CNTs; (G) SEM and (H) EDX of Ru/TiO2/CNTs.
The XRD pattern of CNTs showed typical broad diffraction peaks of the (002) and (100) planes of carbon, while TiO2/CNTs delivered several diffraction peaks attributed to (101), (200), (211), (204), and (440) planes, which were assigned to rutile TiO2 (JCPDS (21-1272) [Figure 3A][29,30]. Notably, no peak for Ru was found in the results of the Ru/TiO2/CNTs due to its low content. X-ray photoelectron spectroscopy (XPS) of the Ru/TiO2/CNTs confirmed the co-existence of Ru, Ti, O, and C elements [Figure 3B], and the binding energy of Ti 2p½ and Ru3p3/2 overlapped at approximately 465 eV. Four individual component peaks can be identified as C-C (284.6 eV), C-O (285.3 eV), C=O (287.5eV), and O-C=O (288.5 eV), respectively
Figure 3. (A) XRD patterns of the pure CNTs, TiO2/CNTs and Ru/TiO2/CNTs samples; (B) XPS spectra of the Ru/TiO2/CNTs; High-resolution XPS spectra for (C) C 1s;
Electrochemical performance analysis
The initial discharge-charge curves of cells with the three samples in the potential range of 2.0-4.5V (vs. Li/Li+) at a current density of 0.1 mA g-1 were measured [Figure 4A]. Cells with Ru/CNTs and Ru/TiO2/CNTs cathodes showed obviously smaller charge overpotential and larger capacities than those of CNTs, because of the high catalytic efficiency of Ru catalyst. Meanwhile, the capacity of Ru/TiO2/CNTs was almost 1000 mAh g-1 higher than that of Ru/CNTs. Both cathodes showed similar initial discharge-charge behavior at a fixed discharge depth. It is worth noting that the discharge overpotential of the Ru/TiO2/CNTs was a bit larger than that without TiO2 [Figure 4B]. We speculate that the low-conductive TiO2 showed a weak effect on the Li2O2 nucleation during the first cycle. However, the discharge terminal potential recovered in the subsequent cycling process. Compared with the cell of Ru/CNTs [Figure 4C], the discharge and charge plots in fixed capacity kept quite stable [Figure 4D]. A rather clear comparison could be observed from the evolution process of the discharge terminal potential with a fixed capacity of 500 mAh g-1. A cycle life of almost 110 was achieved when using the Ru/TiO2/CNTs cathode [Figure 4E]. The prolonged lifespan could be approximately benefited from the thin TiO2 layer that effectively inhibited carbon corrosion and electrolyte loss.
Figure 4. (A) Initial discharge and charge profiles of cells with different cathodes; (B) Initial discharge-charge plots of cells with different cathodes with a capacity limitation of 500 mAh g-1 at a current density of 0.1 mA g-1; Selected discharge-charge curves at different cycles of (C) Ru/CNTs and (D) Ru/TiO2/CNTs (E) Potential-time curves of cells based on different cathodes at a current density of 100 mA g-1 with a fixed specific capacity of 500 mAh g-1.
Discharge and charge mechanism analysis
To further explore how the as-prepared Ru/TiO2/CNTs cathode worked on the mechanism of the Li-O2 battery, the morphological evolution of the cathode was characterized by SEM at different cycling states. The fresh electrode showed a porous structure [Figure 5A]. Snow-like material appeared on the whole surface of the electrode after the first discharge [Figure 5B], but disappeared after recharge [Figure 5C]. The reversible formation and disappearance of the discharge product indicated that the Ru/TiO2/CNTs cathode could probably catalyze the Li2O2 formation and decomposition. More importantly, unlike traditional toroidal-like or film-like discharge products, which either needed large charge overpotential to decompose or totally passivate the electrode surface, the as-prepared Ru/TiO2/CNTs cathode still featured a porous state after discharge and the Li2O2 showed crystalline-like structure with premium size. Thus, the ORR and especially OER kinetics based on such structured-Li2O2 should be remarkably boosted and the above-mentioned electrochemical results powerfully verified this. The electrode surface became not as sharp as the fresh one after 30 cycles, but still porous [Figure 5D]. Agglomeration of porous particles appeared on the cathode when the cycle life reached 60 [Figure 5E], which was probably due to the gradual accumulation of the side product and the uncompleted decomposition of the discharge product. After another further 40 cycles, the surface of the cathode was covered by tough solid materials and could be caused by the long-term degradation of the catalyst and side products [Figure 5F], which also predicted the end of the battery life. As is known, this is the fate of all the Li-O2 batteries until the problems, e.g., electrolyte volatilization/decomposition and carbon oxidation caused by the unique system, can be well solved. The XPS result showed a strong obvious Li 1s peak at 54.68 eV ascribing Li2O2 after the first discharge and the peak disappeared after recharge [Figure 5G], demonstrating that the as-prepared Ru/TiO2/CNTs material could function as a bifunctional catalyst for Li-O2 battery. One should note that there was no Li2O2 signal except a poor peak at 55.52 eV assigning to Li2CO3 appeared on the XPS spectra after 30 cycles. XRD measurements on the cathode at different cycling states were also conducted [Figure 5H]. It showed that the primary discharge product was Li2O2 and the reaction was based on the formation and decomposition of Li2O2. The XRD pattern of the cathode after 30th charge showed overlapped diffraction peaks (36.9°) of Li2CO3 and
Figure 5. SEM images of the Ru/TiO2/CNTs at different discharge stages: (A) fresh; (B) after first discharge; (C) after first recharge; (D) after 30 cycles; (E) after 60 cycles; (F) after 100 cycles; (G) High-resolution XPS spectra of Li 1s of Ru/TiO2/CNTs after first discharged, recharge and 30 cycles; (H) XRD patterns of the Ru/TiO2/CNTs cathode at different discharge/charge stages;
CONCLUSION
To sum up, we designed a Ru/TiO2/CNTs cathode and successfully obtained it via a hydrolysis reaction of the titanium butoxide on the surface of CNTs, followed by aqueous reduction to load Ru. The as-prepared cathode combined consideration of the favorable kinetics of Li2O2-related main reaction and the avoidance of the side reaction caused by carbon cathode. Electrochemical results evidenced that the Ru/TiO2/CNTs cathode could catalyze snow-like Li2O2-formation and more importantly the cathode still featured a porous state after discharge, which suggested quite friendliness on the subsequent charge and cycling process. As a result, the battery with Ru/TiO2/CNTs cathode delivered a discharge capacity of about 4500 mAh g-1 and a long lifespan of 110 at a current density of 100 mAg-1. The concept of this research is of high value in directing the reasonable design of cathode material for Li-O2 batteries.
DECLARATIONS
Authors’ contributionsConceived the manuscript: Liu L, Wu Y
Wrote the manuscript: Liu L, Zhou C, Fang W
Reviewed the manuscript: Liu L, Fang W, Wu Y
The discussion of the manuscript: Liu L, Zhou C, Fang W, Hou Y, Wu Y
Availability of data and materialsNot applicable.
Financial support and sponsorshipThis work was supported by the Key R&D Program of the Ministry of Science and Technology (No. 2021YFB2400201), the National Natural Science Foundation of China (No. 52002171, 22101133, 22279055), the Natural Science Foundation of Jiangsu Province (No. BK20200696, No. BK20200768, No.20KJB430019).
Conflicts of interestAll authors declared that there are no conflicts of interest.
Ethical approval and consent to participateNot applicable.
Consent for publicationNot applicable.
Copyright© The Author(s) 2023.
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Liu L, Zhou C, Fang W, Hou Y, Wu Y. Rational design of Ru/TiO2/CNTs as cathode: promotion of cycling performance for aprotic lithium-oxygen battery. Energy Mater 2023;3:300011. http://dx.doi.org/10.20517/energymater.2022.68
AMA Style
Liu L, Zhou C, Fang W, Hou Y, Wu Y. Rational design of Ru/TiO2/CNTs as cathode: promotion of cycling performance for aprotic lithium-oxygen battery. Energy Materials. 2023; 3(2): 300011. http://dx.doi.org/10.20517/energymater.2022.68
Chicago/Turabian Style
Liu, Lili, Congcong Zhou, Weiwei Fang, Yuyang Hou, Yuping Wu. 2023. "Rational design of Ru/TiO2/CNTs as cathode: promotion of cycling performance for aprotic lithium-oxygen battery" Energy Materials. 3, no.2: 300011. http://dx.doi.org/10.20517/energymater.2022.68
ACS Style
Liu, L.; Zhou C.; Fang W.; Hou Y.; Wu Y. Rational design of Ru/TiO2/CNTs as cathode: promotion of cycling performance for aprotic lithium-oxygen battery. Energy Mater. 2023, 3, 300011. http://dx.doi.org/10.20517/energymater.2022.68
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