Abstract:Manipulating the interfacial structure is vital to enhancing
the
interfacial thermal conductance (G) in Cu/diamond
composites for promising thermal management applications. An interconnected
interlayer is frequently observed in Cu/diamond composites; however,
the G between Cu and diamond with an interconnected
interlayer has not been addressed so far and thus is attracting extensive
attention in the field. In this study, we designed three kinds of
interlayers between a Cu film and a diamond substrate by magnet… Show more
“…In addition, the responsivity of peak current and area of Li 2 S precipitation are crucial indexes to assess the electrochemical activity of solid–liquid transformation of polysulfides. [ 5b,27b ] Specifically, the responsivity of Li 2 S nucleation in Pt SAs/In 2 S 3 /Ti 3 C 2 (Figure 4g) is earlier than those in Super P, In 2 S 3 , Ti 3 C 2 , and In 2 S 3 /Ti 3 C 2 . Those observations demonstrate that Pt SAs/In 2 S 3 /Ti 3 C 2 possesses fast catalytic kinetics of Li 2 S nucleation and precipitation processes.…”
Section: Resultsmentioning
confidence: 97%
“…The unique LiPSs adsorption capability of Pt SAs/In 2 S 3 /Ti 3 C 2 should be from its hierarchical porous structure (Figure S14a, Supporting Information) and the unique adsorption sites between Pt SAs/In 2 S 3 /Ti 3 C 2 and polysulfides. [ 5b,25 ] The interaction between the Pt SAs/In 2 S 3 /Ti 3 C 2 @PP and LiPSs was further investigated by XPS. As exhibited in FigureS14b, Supporting Information, the S 2p spectrum of Li 2 S 6 shows two peaks at 161.4 and 162.8 eV, corresponding to the terminal (ST –1 ) and bridging (SB 0 ) sulfur.…”
Section: Resultsmentioning
confidence: 99%
“…Further, upon the adsorption of Li 2 S 6 , a significant upshift toward higher binding energy can be observed in Pt SAs/In 2 S 3 /Ti 3 C 2 , demonstrating its higher chemical anchoring affinity to LiPSs. [ 5b ] Furthermore, the two additional peaks centered at higher binding energy area of 168.9 and 167.2 eV are assigned to polythionate and thiosulfate, respectively. Meanwhile, both In 3d and Pt 4f peaks of Pt SAs/In 2 S 3 /Ti 3 C 2 ‐Li 2 S 6 shift toward lower binding energy (Figure 4c; Figure S14c, Supporting Information), demonstrating the increased electron density at the metal center and the strong chemical capture capability.…”
Section: Resultsmentioning
confidence: 99%
“…In addition, the Pt SAs/In 2 S 3 / Ti 3 C 2 @PP based cell exhibits the earliest cathodic peaks located at 2.32 V (peak I) and 2.02 V (peak II) and anodic peaks potentials of 2.38 V (peak IV) and 2.35 (peak III), which are assigned to the reduction of S 8 to high soluble LiPSs, Li 2 S 4 to insoluble species (Li 2 S 2 /Li 2 S), and the reverse process, respectively. [ 5b,31 ] From another perspective, [ 5b,32 ] different from the four control samples, the cell with Pt SAs/In 2 S 3 /Ti 3 C 2 @PP delivers the highest onset potentials of cathodic peaks and the lowest onset potentials of anodic peaks (Figure S19b–f and Table S4, Supporting Information), demonstrating the accelerated polysulfides redox kinetics by Pt SAs/In 2 S 3 /Ti 3 C 2 and the dramatic enhancement of the conversion efficiency of liquid–solid polysulfides. Figure S20, Supporting Information, illustrates the CV curves for initial five charges/discharges of Li–S batteries with different PP‐modified separators at a scan rate of 0.1 mV s −1 .…”
Section: Resultsmentioning
confidence: 99%
“…[ 4 ] In particular, the coating of functional materials on the separator stands out for its complementary countermeasure to suppress LiPSs shuttle effect and to regulate lithium dendrite growth. [ 5 ]…”
can suppress the polysulfide shuttling and exhibit excellent redox electrocatalytic properties for lithium polysulfides decomposition. The batteries with heterostructure-modified separators show a high initial discharge capacity of 1068.4 mAh g −1 at 0.5 C, excellent rate performances (719.6 mAh g −1 at 5C), and a remarkable cycling ability. Even with a high sulfur loading of 6.4 mg cm −2 , the pouch cell can deliver an areal capacity of 5.54 mAh cm −2 at 0.2 C. This work not only provides a new route for preparing SA-catalysts, but also sheds new lights into engineering electronic structures of heterointerfaces for developing high-performance Li-S batteries.
“…In addition, the responsivity of peak current and area of Li 2 S precipitation are crucial indexes to assess the electrochemical activity of solid–liquid transformation of polysulfides. [ 5b,27b ] Specifically, the responsivity of Li 2 S nucleation in Pt SAs/In 2 S 3 /Ti 3 C 2 (Figure 4g) is earlier than those in Super P, In 2 S 3 , Ti 3 C 2 , and In 2 S 3 /Ti 3 C 2 . Those observations demonstrate that Pt SAs/In 2 S 3 /Ti 3 C 2 possesses fast catalytic kinetics of Li 2 S nucleation and precipitation processes.…”
Section: Resultsmentioning
confidence: 97%
“…The unique LiPSs adsorption capability of Pt SAs/In 2 S 3 /Ti 3 C 2 should be from its hierarchical porous structure (Figure S14a, Supporting Information) and the unique adsorption sites between Pt SAs/In 2 S 3 /Ti 3 C 2 and polysulfides. [ 5b,25 ] The interaction between the Pt SAs/In 2 S 3 /Ti 3 C 2 @PP and LiPSs was further investigated by XPS. As exhibited in FigureS14b, Supporting Information, the S 2p spectrum of Li 2 S 6 shows two peaks at 161.4 and 162.8 eV, corresponding to the terminal (ST –1 ) and bridging (SB 0 ) sulfur.…”
Section: Resultsmentioning
confidence: 99%
“…Further, upon the adsorption of Li 2 S 6 , a significant upshift toward higher binding energy can be observed in Pt SAs/In 2 S 3 /Ti 3 C 2 , demonstrating its higher chemical anchoring affinity to LiPSs. [ 5b ] Furthermore, the two additional peaks centered at higher binding energy area of 168.9 and 167.2 eV are assigned to polythionate and thiosulfate, respectively. Meanwhile, both In 3d and Pt 4f peaks of Pt SAs/In 2 S 3 /Ti 3 C 2 ‐Li 2 S 6 shift toward lower binding energy (Figure 4c; Figure S14c, Supporting Information), demonstrating the increased electron density at the metal center and the strong chemical capture capability.…”
Section: Resultsmentioning
confidence: 99%
“…In addition, the Pt SAs/In 2 S 3 / Ti 3 C 2 @PP based cell exhibits the earliest cathodic peaks located at 2.32 V (peak I) and 2.02 V (peak II) and anodic peaks potentials of 2.38 V (peak IV) and 2.35 (peak III), which are assigned to the reduction of S 8 to high soluble LiPSs, Li 2 S 4 to insoluble species (Li 2 S 2 /Li 2 S), and the reverse process, respectively. [ 5b,31 ] From another perspective, [ 5b,32 ] different from the four control samples, the cell with Pt SAs/In 2 S 3 /Ti 3 C 2 @PP delivers the highest onset potentials of cathodic peaks and the lowest onset potentials of anodic peaks (Figure S19b–f and Table S4, Supporting Information), demonstrating the accelerated polysulfides redox kinetics by Pt SAs/In 2 S 3 /Ti 3 C 2 and the dramatic enhancement of the conversion efficiency of liquid–solid polysulfides. Figure S20, Supporting Information, illustrates the CV curves for initial five charges/discharges of Li–S batteries with different PP‐modified separators at a scan rate of 0.1 mV s −1 .…”
Section: Resultsmentioning
confidence: 99%
“…[ 4 ] In particular, the coating of functional materials on the separator stands out for its complementary countermeasure to suppress LiPSs shuttle effect and to regulate lithium dendrite growth. [ 5 ]…”
can suppress the polysulfide shuttling and exhibit excellent redox electrocatalytic properties for lithium polysulfides decomposition. The batteries with heterostructure-modified separators show a high initial discharge capacity of 1068.4 mAh g −1 at 0.5 C, excellent rate performances (719.6 mAh g −1 at 5C), and a remarkable cycling ability. Even with a high sulfur loading of 6.4 mg cm −2 , the pouch cell can deliver an areal capacity of 5.54 mAh cm −2 at 0.2 C. This work not only provides a new route for preparing SA-catalysts, but also sheds new lights into engineering electronic structures of heterointerfaces for developing high-performance Li-S batteries.
In the process of upgrading energy storage structures, sodium‐ion batteries (SIBs) are regarded as the most promising candidates for large‐scale grid storage systems. However, the difficulty in further improving their specific capacity and lifespan has become a major obstacle to promoting extensive application. Herein, by optimizing synthesis conditions, a biphasic‐Na2/3Ni1/3Mn2/3O2 cathode that exhibits an ultrahigh capacity of ≈200 mAh g‐1 without the involvement of anion redox reactions is successfully synthesized. Nevertheless, there is significant electrochemical performance degradation because of failure at the cathode‐electrolyte interface as revealed by comprehensive analyses. Further in‐depth research proves that the surface side reactions that occur at high operating voltages and the transition metal dissolution that occurs in low voltage are the root causes of electrode surface failure. Therefore, the metal oxide atomic layer deposition (ALD) protective layer is deliberately chosen to suppress such failures. The coating effectively blocks corrosion of the cathode material by the electrolyte and successfully anchors the transition metal ions on the particle surface. As a result, the cycle stability and rate performance of the electrode are improved considerably. This surface engineering strategy could provide concepts with broad applicability for suppressing the failure of sodium layered cathodes.
Compared with conventional positive electrode materials in Li‐ion batteries, Li‐rich materials have a huge advantage of large specific capacities of >300 mAh g−1. Anionic redox mechanism is proposed to explain the over‐capacity, which means anions can participate in the redox process for charge compensation. The concept enriches the range and design considerations of high‐energy‐density positive electrode materials for both Li‐ion and Na‐ion batteries, which therefore arouses extensive attention. This review summarizes the progress of anionic redox in rechargeable batteries in recent years and discusses the fundamental mechanism that triggers anionic redox. Moreover, the state‐of‐the‐art materials involving anionic redox are illustrated, accompanied by the challenges for practical applications. Furthermore, the common techniques for monitoring anionic redox are reviewed and compared for an advisable choice in future studies. Finally, the consideration and discussion for designing stable positive electrodes based on cationic and anionic redox are presented. The perspective is highlighted and this review provides a basic understanding of anionic redox in rechargeable batteries and paves the way to develop high‐capacity positive electrodes for high‐energy battery systems.
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