Fabrication of lightweight alumina with nanoscale intracrystalline pores

Fu, Lvping; Gu, Huazhi; Huang, Ao; Zou, Yongshun; Zhang, Mei‐Jie

doi:10.1111/jace.16914

Cited by 31 publications

(18 citation statements)

References 18 publications

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“…1(a) was fabricated by stacking the ceramic green sheets (on which each material is printed) and subsequent co-sintering. This battery works at ∼2.3 V (LCP (4.8 V vs. Li/Li + ) 38,39 to LATP (2.5 V vs. Li/Li + ) 40,41 ) at 120°C (see details in the ESI S1 †).…”

Section: Sample Preparationmentioning

confidence: 99%

Internal potential mapping of charged solid-state-lithium ion batteries using in situ Kelvin probe force microscopy

et al. 2017

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Solid-state-lithium ion batteries (SS-LIBs) are a promising candidate for next-generation energy storage devices. Novel methods for characterizing electrochemical reactions occurring during battery operation at the nanoscale are highly required for understanding the fundamental working principle and improving the performance of the devices. In this work, we combined Ar ion milling under non-atmospheric conditions with in situ cross-sectional Kelvin probe force microscopy (KPFM) for direct imaging of the internal electrical potential distribution of the SS-LIBs. We succeeded in the direct visualization of the change in the potential distribution of a cathode composite electrode (a mixture of the active materials, solid electrolytes, and conductive additives) arising from battery charging (electrochemical reaction). The observed results provided several insights into battery operation, such as the behavior of Li ions and inhomogeneity of electrochemical reactions in the electrode. Our method paves the way to characterize the fundamental aspects of SS-LIBs for the improvement of device performance, including the evaluation of the distribution of the Li ion depleted regions, visualization of the conductive paths, and analysis of the cause of degradation.

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Section: Sample Preparationmentioning

confidence: 99%

Internal potential mapping of charged solid-state-lithium ion batteries using in situ Kelvin probe force microscopy

et al. 2017

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“…Table 3 gives the comparison between sample 3‐SJ and existing lightweight porous materials in previous reports. Although the same material and a similar amount of the same pore‐forming agent were used by Fu and Wang et al, 24,35 the thermal conductivity in the present work is much lower and the cold compressive strength is much higher. Note that the performances in present work are also quite excellent comparing with lightweight alumina using modification methods.…”

Section: Resultsmentioning

confidence: 70%

“…9 Table 3 gives the comparison between sample 3-SJ and existing lightweight porous materials in previous reports. Although the same material and a similar amount of the same pore-forming agent were used by Fu and Wang et al, 24,35 the thermal conductivity in the present work is much lower and the cold compressive strength is much higher. Note that the performances in present work are also 25 Some other researchers also fabricated porous alumina ceramics with higher porosity (67.7%); however, the lower thermal conductivity (0.248 W/m•K) and lower cold compressive strength (29.2 MPa) were obtained at the same time.…”

Section: Phase Analysis Microstructure and Thermal Conductivity Omentioning

confidence: 66%

Preparation of high‐strength lightweight alumina with plant‐derived pore using corn stalk as pore‐forming agent

et al. 2020

Int J Applied Ceramic Tech

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To improve the mechanical and thermal insulation properties of lightweight alumina, which was prepared by using pore‐forming agent from biological sources, the silica sol‐infiltrated corn stalk was utilized. Spring back and hygroscopicity of corn stalk powder as well as cold compressive strength, thermal conductivity, microstructure, and pore size distribution of lightweight alumina were characterized. The results indicate that impregnation of silica sol leads to different degrees of decrease in spring back height due to achieving better mesh by silica gel between the corn stalk powders, and then improves the formability, although at the same time the large number of hydrophilic groups results in an increase in hygroscopicity. Furthermore, sol impregnated pore‐forming agent optimizes the microstructure of the lightweight alumina pores. Lightweight alumina with a cold compressive strength up to 48.64 MPa was produced, and with the silica sol concentration of 3 wt%, lower thermal conductivity values at all test temperatures were obtained. Hence, the use of corn stalk impregnated with the appropriate concentration of silica sol as pore‐forming agent could enhance the mechanical and thermal insulation properties of lightweight alumina for the spheroidization of pore shape, randomization of pore distribution as well as miniaturization of pore size.

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“…A highly resistive thin amorphous layer was detected between two neighboring grains with a large lattice orientation (Type A), while a thicker transition layer containing dislocations to block ionic transport occurred between two grains with a similar lattice orientation (Type B). Some phases, i.e., Li [85][86][87][88][89][90] can be doped into the NASICON-type fast ionic conductors to tune their conductivity. Compared with pristine conductors, notable enhancements have been described for Li-doped LAGP (1.9 × 10 −4 S cm −1 ), [85] B 2 O 3 -doped LAGP (6.9 × 10 −4 S cm −1 ), [86] Li 2 O-doped LAGP (7.25 × 10 −4 S cm −1 ), [87] SiO 2 -doped LATP (over 10 −3 S cm −1 ), [88] Y 2 O 3 -doped LAGP (5 × 10 −4 S cm −1 ), [77] and Bi 2 O 3 -doped LATP (9.4 × 10 −4 S cm −1 ).…”

Section: Garnet-type Ssesmentioning

confidence: 99%

“…Some phases, i.e., Li [85][86][87][88][89][90] can be doped into the NASICON-type fast ionic conductors to tune their conductivity. Compared with pristine conductors, notable enhancements have been described for Li-doped LAGP (1.9 × 10 −4 S cm −1 ), [85] B 2 O 3 -doped LAGP (6.9 × 10 −4 S cm −1 ), [86] Li 2 O-doped LAGP (7.25 × 10 −4 S cm −1 ), [87] SiO 2 -doped LATP (over 10 −3 S cm −1 ), [88] Y 2 O 3 -doped LAGP (5 × 10 −4 S cm −1 ), [77] and Bi 2 O 3 -doped LATP (9.4 × 10 −4 S cm −1 ). [89] For example, excess Li will segregate at the GBs and form a Lirich structure in the LAGP (Figure 3d), being beneficial for Li + ion migration across the GBs through reducing the activation energy and increasing the concentration of charge carriers.…”

Section: Garnet-type Ssesmentioning

confidence: 99%

Interfacial Incompatibility and Internal Stresses in All‐Solid‐State Lithium Ion Batteries

Liu

et al. 2019

Advanced Energy Materials

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The continuous depletion of fossil fuels, the increase of oil prices, and the need to decrease CO 2 emissions have stimulated intensive research on developing alternative renewable and clean energy sources. [1] Among these alternative energy sources, rechargeable Li-ion batteries (LIBs) are one of the promising candidates. To date, the LIBs basically consisting of a positive electrode (cathode), an electrolyte, and a negative electrode (anode) have widespread applications, such as portable electronic devices, pure electric vehicles (PEVs), and hybrid electric vehicles (HEVs). [2] The state-of-the-art electrolytes are usually the lithium salts (LiPF 6 , LiBF 4 , and LiCF 3 SO 3 ) dissolved in organic solvents, i.e., ethylene carbonate, propylene carbonate, polyethylene oxide, and dimethyl carbonate, [3] which exhibit excellent wetting of the electrodes and produce a fast transfer of Li + ions upon charging and discharging. However, they suffer from flammability, poor electrochemical stability, limited temperature range of operation, and low power density. [4] There is an ever-increasing demand for batteries with a higher energy and power density, although current LIBs offer volumetric and gravimetric energy densities up to 770 Wh L −1 and 260 Wh kg −1 , respectively. [5] To improve the energy/power density of LIBs, one way is to adopt high-potential cathode materials such as LiNi 0.5 Mn 1.5 O 4 (LNMO). The high-voltage plateau of LNMO (≈4.7 V vs Li/Li + ) makes its energy density 20-30% higher than the energy density of commercial LiCoO 2 and LiFePO 4 . [6] However, successful commercialization of the LNMO is restricted in high-energy LIBs due to electrolyte decomposition and side reaction of the cathodes and liquid electrolytes when operating at high voltages. [7,8] The other way to improve the energy/power density is to replace the conventional graphite anode with Li metal. The Li metal, with a low anode potential (−3.04 V vs standard hydrogen electrode) and high specific capacity (3862 mAh g −1 for the Li anode versus 372 mAh g −1 for the graphite anode), [9][10][11] has been considered as the "Holy Grail" of battery technologies. When paired with sulfur and oxygen, the theoretical energy density of Li-S (≈2567 Wh kg −1 ) and Li-O 2 (≈3505 Wh kg −1 ) batteries is far higher than the theoretical energy density of conventional LIBs (≈387 Wh kg −1 ). [12][13][14][15] When Li metal approaches the liquid electrolytes, however, unstable Li/electrolyte interface Rechargeable Li-ion batteries (LIBs) are electrochemical storage device widely applied in electric vehicles, mobile electronic devices, etc. However, traditional LIBs containing liquid electrolytes suffer from flammability, poor electrochemical stability, and limited operational temperature range. Replacement of the liquid electrolytes with inorganic solid-state electrolytes (SSEs) would solve this problem. However, several critical issues, such as poor interfacial compatibility, low ionic conductivity at ambient temperatures, etc., need to be surmounted befor...

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Fabrication of lightweight alumina with nanoscale intracrystalline pores

Cited by 31 publications

References 18 publications

Internal potential mapping of charged solid-state-lithium ion batteries using in situ Kelvin probe force microscopy

Internal potential mapping of charged solid-state-lithium ion batteries using in situ Kelvin probe force microscopy

Preparation of high‐strength lightweight alumina with plant‐derived pore using corn stalk as pore‐forming agent

Interfacial Incompatibility and Internal Stresses in All‐Solid‐State Lithium Ion Batteries

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