Yan Wang1*
Zeshunji Luo
Licai Fu- 1The 18th Research Institute of China Electronics Technology Group Corporation, Tianjin, China
- 2College of Material Science and Engineering, Hunan University, Changsha, China
The thermal battery has been designed to be active at high temperature to satisfy storage life and large capacity for storage and emergency power. The development of thermal battery with high specific energy requires that the cathode has high thermal stability and excellent conductivity. Here, the semiconductor material Li–Cu–O compounds LiCu2O2 and LiCu3O3 are synthesized by a simple solid-phase sintering technique, which is simpler than the traditional synthesis process. The thermal decomposition temperatures are 680°C and above 900°C, respectively. This work first applies the Li–Cu–O compounds to the thermal battery. With a cutoff voltage of 1.5 V, the specific capacities of LiCu2O2 and LiCu3O3 are 423 and 332 mA h g−1. Both the decomposition temperature and specific capacity are higher than in the commercial FeS2 and CoS2, especially LiCu2O2. This work affords an alternative of the cathode materials for high specific capacity thermal battery.
Introduction
The copper-oxide-based material has been investigated as a high-temperature superconductor, LiBs electrode, and catalyst because of its good electrical conductivity, presence of electron holes, and magnetic interactions (Nakamura et al., 2006; Lepple et al., 2017). Of course, copper oxide itself has become the focus of investigations because of its microstructural details, conductivity, and electron structure (Xu et al., 2019). Interest in the system Li–Cu–O also evolved from cathode material for special battery, where a potential usage of Li/CuO thermal battery was considered (Liao et al., 2020). As a primary battery, thermal battery can only be activated when the temperature reached the melting point of eutectic salts electrolyte (Guidotti and Masset, 2006; Masset and Guidotti, 2007; Jeong et al., 2019). This special feature makes the thermal battery have a long shelf-life, excellent mechanical robustness, and being able to supply high output power; it has been used as power sources for guided missiles and proximity fuzes in ordinance devices (Masset and Guidotti, 2007). The cathode materials with poor thermal stability and low specific capacity limit the further development and application of thermal battery.
The Li–Cu–O compounds with a high initial charge capacity are candidates for a new cathode material, such as Li2CuO2 and LiCuO2 (Vitins et al., 2003; Nakamura et al., 2005; Prakash et al., 2005; Arachi et al., 2012; Zhang et al., 2018). Besides, the well-known lithium copper oxides LiCu2O2 and LiCu3O3 with mixed valent copper are unique in the Li–Cu–O system, which gives rise to high Tc behavior and are semiconductor with ρ293K of 106 and 0.1 Ω cm (Goshall, 1986; Hibble et al., 1990; Roessli et al., 2001; Bush and Kamentsev, 2004; Zhu et al., 2011; Kamentsev et al., 2013; Lepple et al., 2013; Ivanov et al., 2014; Bush et al., 2018). Additionally, LiCu2O2 and LiCu3O3 show excellent thermal stability (Hibble et al., 1990; Bush et al., 2004, 2019), which makes them good cathodes for thermal battery. Based on X-ray emission and photoelectron spectra, the valence states of the their Cu atoms are found to be mixed univalent (CuI) and divalent (CuII) (Lin et al., 1996; Zatsepin et al., 1998).
However, it is not easy to obtain a pure single or polycrystalline LiCu2O2 or LiCu3O3 phase. CuO, Cu2O, and Li2CuO2 are typical impurities for them (Paszkowicz et al., 2001). Because some Li2O or Li2CO3 are lost during heating, this leads to the formation of CuO and Cu2O (Hibble et al., 1990). LiCu2O2 and LiCu3O3 would be oxidized, forming Li2CuO2 at lower temperatures of 310–790°C with oxygen (Bush et al., 2004, 2019). Hence, a majority of synthetic methods for LiCu2O2 and LiCu3O3 choose quenching from 800 to 900°C. In addition, homogenizing and reheating are necessary to ensure the uniformity and purity of the product. In order to simplify synthetic methods, the raw materials are mixed by ball mill before being heat treated in this work. Moreover, to keep the high purity, both the synthesis process of LiCu2O2 and the cooling process of LiCu3O3 are carried out in Ar. Additionally, the micromorphology of LiCu2O2 and LiCu3O3 and their electrochemical performance as cathode materials for thermal batteries were studied.
Experimental
Material Synthesis
All starting materials (Table 1) are purchased from commercial sources and used without further purification. Shiny polycrystalline powders of the LiCu2O2 and LiCu3O3 are prepared by a simple solid-state method.
Table 1. Chemical reagents used in the experiment.
As shown in the Figure 1, the raw materials for LiCu2O2, Li2CO3, Cu2O, and CuO are put into an agate jar with agate balls (ball-to-powder weight ratio of 10:1) in a 1:1:2 ratio, and anhydrous ethanol is applied as a solvent. The raw materials are grounded in a ball mill (Tencan powder QXQM-2) for 6 h at a rotation speed of 400 rpm and dried to absolute at 80°C in an air-drying oven (Jinghong DHG-9070A). Subsequently, the mixtures are heat treated at 700°C for 7 h in a tube furnace under flow argon atmospheres with heating and cooling rates of 10°C min−1. In order to synthesize the LiCu3O3, Li2O·4CuO is mixed in the same way as raw materials for LiCu2O2 and then is heat-treated at 880°C for 7 h under flow argon–oxygen mixed atmospheres with heating and cooling rates of 10°C min−1 (cooling process only under argon). Dark brown powders of the LiCu2O2 and black powders of the LiCu3O3 are ground and keep in air.
Figure 1. Synthesis route of LiCu2O2 and LiCu3O3 powders.
Materials Characterization
The phase structures of Li–Cu–O are determined by X-ray diffraction (XRD) on a Mini Flex 600 from 5° (2θ) to 90° (2θ) with Cu-Kα radiation (λ = 0.154178 nm) and X-ray photoelectron spectroscopy (XPS) on a Thermo Fisher Scientific K-ALPHA. For all XRD measurements, the resolution in the scans is kept at 0.01° with a rate of 10° min−1. Thermogravimetric analysis (TG, Henven HCT-4) is conducted with a heating rate of 10°C min−1 from room temperature to 900°C and a 50 ml min−1 Ar flowrate. The analyses of the microstructures of Li–Cu–O are performed using a scanning electron microscope (SEM, FEI Quanta 200) and a transmission electron microscope (TEM, FEI Tecnai G2 60-300).
Preparation of a Single Thermal Battery Cell and Discharge Test
The single cell was conventionally assembled by lamination. The 0.6 mm Li–B alloy was punched into a disk with a diameter of 17.5 mm as anode. The separator contains 50 wt.% ternary all-lithium eutectic salt electrolyte (LiF–LiCl–LiBr, m.p. = 436°C) and 50 wt.% MgO. Both the cathode (0.15 g Li–Cu–O) and separator were prepared into Φ 17.5 mm by powder tableting process. The cell was assembled in a glove box with the water and oxygen content being <5 ppm.
Discharge performances are evaluated on an IT8511 plus the single-channel programmable electronic load (ITECH). The single cell was sandwiched between two collectors. Before the tests, the temperature-controlled stainless steel cylinder heater was heated from room temperature to 500°C. The discharge current density is 0.1 A cm−2 with the cutoff voltage of 1.5 V (75% of the peak voltage) at 500°C.
Results and Discussion
The XRD patterns of both powders closely agreed with LiCu2O2 (#81-0344) and LiCu3O3 (#81-0345), respectively (Figure 2). The as-grown crystals contain only traces of foreign phases (LiCuO, Cu2O, and CuO). The purity of the quantitative analysis of the powder diffraction patterns are 93.1 wt.% LiCu2O2 and 93.7 wt.% LiCu3O3, which were calculated by K value method according to Table 2. The reason why impurity phase such as Cu2O or CuO existed on samples may be the loss of Li2CO3 or Li2O during prolonged heating (Hibble et al., 1990), while the LiCuO can be attributed to the uncomplete reaction during synthesis process. The high-resolution transmission electron microscopy (HRTEM) presented that the main composition is LiCu2O2 or LiCu3O3 (Figures 2b,c). A few retained phases, such as CuO, and Cu2O, can also be detected. These results verified that LiCu2O2 and LiCu3O3 were prepared successfully.
Figure 2. (a) The X-ray diffraction (XRD) patterns and high-resolution transmission electron microscopy (HRTEM) images of (b) LiCu2O2 and (c) LiCu3O3.
Table 2. The information of X-ray diffraction (XRD) patterns of synthesized LiCu2O2 and LiCu3O3.
The chemical state of LiCu2O2 and LiCu3O3 was studied using XPS (Figures 3A–F). Their XPS core-level spectra of Cu 2p comprise intense spin-orbit split peaks for 2p 3/2 (934.1 eV) and 2p 1/2 (954.2 eV) accompanied by satellite peaks (939–945 eV and 959–964 eV), which are typical of CuII valency (Zatsepin et al., 1998; Momeni and Sedaghati, 2018). Besides, the remaining two main fitted peaks center at 932.4 and 952.5 eV, representing Cu 2p3/2 and Cu 2p1/2 of CuI, respectively (Wang et al., 2018; Zhou et al., 2018). The O 1s peaks located at binding energies of 531.1 and 531.6 eV are in good agreement with the reported values of Cu2O and CuO, respectively (Han et al., 2018). According to the XRD patterns (Figure 2a), the impurity phases of synthesized LiCu2O2 and LiCu3O3 are Cu2O and CuO, respectively. Thus, CuII in LiCu2O2 and CuIin LiCu3O3 can only come from themselves. To sum up, the coexistence of CuI and CuII ions in LiCu2O2 and LiCu3O3 can be concluded.
Figure 3. The X-ray photoelectron spectroscopy (XPS) spectra of (A–C) LiCu2O2 and (D–F) LiCu3O3.
The LiCu2O2 consisted of many uniform distributed clusters with an average size of about 1 μm (Figure 4a), which increased the compaction density of the cathode. The local high magnification showed that these clusters were composed of LiCu2O2 nanograins and impurity-phase Cu2O (Figures 2b, 4b). Both the statistical data and the XRD pattern indicated that the average grain size is about 40 nm, which is beneficial to shortening the migration path of lithium ion, while the roughness surface of clusters could improve the activation sites of the electrochemical reaction and contact area between the cathode and fusional electrolyte. The roughness of the particle might be caused by the composition of nanograins. However, the cluster size of LiCu3O3 increased to 2–15 μm, which were composed of 20–200 nm grains (Figures 4c,d). This size distribution range was far larger than LiCu2O2. Thus, it could be expected that the discharge performance of LiCu2O2 would be more excellent than that of LiCu3O3.
Figure 4. The scanning electron microscopy (SEM) and transmission electron microscopy (TEM) images of (a,b) LiCu2O2 and (c,d) LiCu3O3.
Thermal stability is one of the important indicators for thermal battery cathode (Jin et al., 2018; Luo et al., 2020). As shown in Figure 5A, LiCu2O2 began to decompose to LiCuO, Cu2O, and O2 at around 680°C. The weight loss at 380°C was about 1.81%, which was mainly caused by the decomposition of Li2CO3. Due to the lower content and poor crystallinity, the auxiliary material Li2CO3 could not be detected in XRD. Since there is no Li2CO3 as the reactant, this weight loss peak cannot be observed in the TG curve of LiCu3O3 (Figure 5B). Unlike the LiCu2O2, the LiCu3O3 was kept stable below 900°C with a weight loss <1.0%. In summary, both of them have great thermal stability compared with the conventional thermal battery cathodes, such as FeS2 and CoS2 (Masset and Guidotti, 2008). The high temperature stability completely satisfied the temperature requirements of thermal battery during actual discharge.
Figure 5. The thermogravimetric analysis (TG) curves of LiCu2O2 (A) and LiCu3O3 (B).
The LiCu2O2 and LiCu3O3 presented excellent electrochemical performance (Figure 6). The voltage of LiCu2O2 quickly increased to a peak value of 2.06 V once the thermal battery is activated, in which the impurity phase Cu2O of LiCu2O2 might belong. It is below 2–3 s, which is far shorter than in the secondary Li+ or Li metal battery during larger current discharge. The relative steady voltage platforms were 1.95 and 1.72 V, which were about 0.4 V lower than the theoretical values (Patat et al., 1991; Lepple et al., 2013) due to the resistance of the actual discharge. The voltage of LiCu2O2 gradually decreased along with three steps during discharge. The LiCu3O3 also showed similar discharge characterizations. It should be noted that the peak voltage of LiCu3O3 reached about 2.12 V. This high voltage spike is shown by the raw material CuO, which was significantly enhanced in LiCu3O3 during the initial discharge (Liao et al., 2020). The discharge time is the key factor to the practical application of thermal battery in the field of defense. In this case, the discharge time of LiCu2O2 reached 997 s with high cutoff voltage of 1.5 V at large current density of 0.1 A cm−2. The corresponding specific capacity was 423 mA h g−1. Since the LiCu3O3 particle has a large size and ununiform distribution, it showed a lower specific capacity of 332 mA h g−1, but it is still higher than that of commercial FeS2 of 210 mA h g−1 and CoS2 of 250 mA h g−1. Both LiCu2O2 and LiCu3O3 have excellent conductivity and thermal stability.
Figure 6. The discharge curves of LiCu2O2 (A) and LiCu3O3 (B).
After discharge, the cross-section between LiCu2O2 and electrolyte showed relatively clear interface and particle characters (Figures 7a,b). The Cu elemental mapping also indicated that few Cu diffused from the cathode into the electrolyte (Figure 7c). This interface for LiCu3O3 thermal battery became blurry, and some Cu can be detected into the electrolyte (Figures 7d–f). The thickness of LiCu3O3 cathode varies more than that of LiCu2O2 cathode. This phenomenon is known in thermal battery as high solubility in molten salt, which degrades the battery's performance (Jin et al., 2017). For this reason, the performance of LiCu3O3 thermal battery is worse than that of LiCu2O2 thermal battery. It is demonstrated that LiCu2O2 could keep the structure at high temperature instead of being molten, forming blurry interface for LiCu3O3. To sum up, their discharge performance, especially for LiCu2O2 cathode, provides a new idea for improving the specific capacity of CuO and Cu2O. LiCu2O2 and LiCu3O3 are suitable for use as cathode materials for thermal battery with long life and high specific capacity.
Figure 7. The images of cathode and electrolyte before discharge, cross-sectional SEM image, and corresponding Cu distribution of thermal battery after discharge: (a–c) LiCu2O2 and (d–f) LiCu3O3.
Conclusions
The thermal battery is a kind of Li metal primary battery. The characteristics of high temperature, large current, and long working life of the cathode material require it to have high temperature stability and high specific capacity. In this paper, high-purity LiCu2O2 and LiCu3O3 were synthesized by combining simple mechanical ball mill and solid-phase sintering technique. By considering the excellent thermal stability and high specific capacity for both LiCu2O2 and LiCu3O3, this work developed two new cathode materials for thermal battery (LiCu2O2 or LiCu3O3|LiF-LiCl-LiBr|LiB). The electrochemical tests showed that both cathodes exhibited excellent specific capacity. Especially for the LiCu2O2, the actual specific energy was up to 423 mA h g−1 with cutoff voltage of 1.5 V at 0.1 A cm−2 and 500°C. It was higher than the commercial thermal battery cathodes such as FeS2 and CoS2. This paper indicates that LiCu2O2 and LiCu3O3 are promising cathode materials with the high specific capacity for thermal battery.
Data Availability Statement
The raw data supporting the conclusions of this article will be made available by the authors, without undue reservation.
Author Contributions
YW and LF contributed to conception and design of the study. ZL and LF organized the database. YW and XB performed the statistical analysis. YW wrote the first draft of the manuscript. XB, ZL, and LF wrote sections of the manuscript. All authors contributed to manuscript revision, read, and approved the submitted version.
Funding
The research was carried out with financial support from the Young Teacher Development Program of Hunan University (No. 2015031).
Conflict of Interest
YW and XB were employed by the company The 18th Research Institute of China Electronics Technology Group Corporation.
The remaining authors declare that the research was conducted in the absence of any commercial or financial relationships that could be construed as a potential conflict of interest.
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Keywords: cathode material, thermal battery, high specific capacity, LiCu2O2, LiCu3O3
Citation: Wang Y, Bai X, Luo Z and Fu L (2020) High Specific Capacity Thermal Battery Cathodes LiCu2O2 and LiCu3O3 Prepared by a Simple Solid Phase Sintering. Front. Chem. 8:575787. doi: 10.3389/fchem.2020.575787
Received: 24 June 2020; Accepted: 09 September 2020;
Published: 23 October 2020.
Edited by:
Xiaolei Wang, University of Alberta, CanadaReviewed by:
Dan Luo, University of Waterloo, CanadaWook Ahn, Soonchunhyang University, South Korea
Jingde Li, Hebei University of Technology, China
Copyright © 2020 Wang, Bai, Luo and Fu. This is an open-access article distributed under the terms of the Creative Commons Attribution License (CC BY). The use, distribution or reproduction in other forums is permitted, provided the original author(s) and the copyright owner(s) are credited and that the original publication in this journal is cited, in accordance with accepted academic practice. No use, distribution or reproduction is permitted which does not comply with these terms.
*Correspondence: Yan Wang, NTQ5NTU4NyYjeDAwMDQwO3FxLmNvbQ==; Licai Fu, bGZ1JiN4MDAwNDA7aG51LmVkdS5jbg==