Wiley

Advanced Functional Materials

Published by Wiley

Online ISSN: 1616-3028

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Print ISSN: 1616-301X

Disciplines: Materials science

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Schematic of the working principle of a sodium‐ion battery.
Schematic representation showing the classification of sodium layered oxide.
a) Charge–discharge curves for O3‐NaFeO2. Reproduced by permission.[³²] Copyright 1994, Elsevier. b) Galvanostatic charge–discharge curve for Na/Na0.6[Fe0.5Mn0.5]O2 c) Na/Na0.6[Fe0.5Mn0.5]O2 cycled within (1.5–4.3) V at 12 mA g⁻¹. d) Comparison of cyclic discharge capacity retention for two cathodes. e) Rate capability of Na/Na0.6[Fe0.5Mn0.5]O2 at varying C rates. Before the rate test, the cell was charged to 4.2 V at 0.05 C (13 mA·g⁻¹), then discharged to 1.5 V at different rates ranging (0.05–4) C. The active mass loading on Al current collector was 8.4 mg cm⁻². Reproduced with permission.[³⁵] Copyright 2012, Springer Nature. f) Capacity versus applied potential plots at various Fe compositions for 10 cycles. Reproduced with permission.[³⁷] Copyright 2014, American Chemical Society.
a) Schematic of the various stable phases of NaxMnO2 based on sodium content. Colored region depicts the single‐phase region, while dotted lines represent a possible expansion of phases due to varying synthetic conditions. Reproduced with permission.[42b] Copyright 2022, American Chemical Society. b) Factors that affect the phases of NaxMnO2 crystal systems.
a) A schematic of the primitive NaMnO2. b) Charge–discharge profile for the O′3‐type NaxMnO2. Reproduced with permission.[⁵⁷] Copyright 2011, IOP Publishing. c) Orthorhombic projections of the Mn‐section O′3‐type NaxMnO2. Reproduced with permission.[64b] Copyright 2010, Elsevier. d) Charge–discharge profile curve of the Na2/3MnO2. e) Sub‐micrometer‐sized morphology. Reproduced with permission.[67b] Copyright 2014, American Chemical Society.

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Unleashing the Potential of Sodium‐Ion Batteries: Current State and Future Directions for Sustainable Energy Storage

July 2023

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Advanced Functional Materials, part of the prestigious Advanced portfolio and a top-tier materials science journal, publishes outstanding research related to improving chemical and physical properties of materials.
By covering a broad scope and providing breakthrough research on all aspects of materials science, our readers range from materials scientists, chemists, physicists, and engineers, together with biologists and medical researchers.
The Advanced portfolio from Wiley is a family of globally respected, high-impact journals that disseminates the best science from well-established and emerging researchers so they can fulfill their mission and maximize the reach of their scientific discoveries.

Recent articles


Superior Impact Resistance in Bionic Nanocellulose Composite Supramolecular Elastomers via Multiple Hydrogen Bonding Interactions
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  • Publisher preview available

December 2024

Tianhao Wu

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Hao Jiang

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Yujing Zheng

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Meishuai Zou

Inspired by biological mechanisms of impact protection, nanocellulose and linear polyurethane molecular chains are simultaneously tailored and expanded using supramolecular chemistry. This approach has led to the development of a novel impact protection strategy that leverages multilevel hydrogen bonding interactions. These abundant interactions effectively hinder the crystallization of polycaprolactone (PCL) chain segments, resulting in uniformly distributed microphase separation. This configuration achieves a significant fracture strength of 47.5 MPa, while maintaining an exceptional elongation at a break of 974.2%. The results demonstrate that supramolecular polyurethane‐cellulose nanofiber (SPU‐CNF) elastomer significantly reduces impact force and extends the impact buffer time. Crucially, the underlying mechanisms responsible for energy dissipation and impact protection in SPU‐CNF are elucidated. To validate these properties, impact protection tests at varying impact rates are conducted, underscoring the potential applications of the proposed SPU‐CNF in impact‐resistant materials.


Design and characterization of the PAGs. a), Diagram of the chemical structures of the A component, B component, and cured PAG. b), FTIR spectra of the components of PAG showing the stretching vibration bands of CH2O, NCO, and CO in the A component and NH in the B component. c), ¹HNMR spectra of the components of PAG. d), Rheological properties of PAG. The upper curves display the viscosities of the components, whereas the lower curves reveal the curing behavior of PAG. The intersection of the storage modulus and loss modulus was considered to indicate the gelation time of the PAG. e), Swelling behaviors of PAGs with different degrees of crosslinking and the commercial product Coseal. f), Tensile elastic moduli of the PAGs and Coseal before and after swelling. g), Strain simulation analysis of PAG (bottom) and Coseal (top) using COMSOL software.
Adhesive performance of PAG. a), Diagram of the mechanism through which PAG binds to arterial tissue. b), SEM image of the interface between the bioglue and the arterial wall (scale bar: 25 µm). c–d), Typical curves and histogram of the lap shear adhesion of PAG and Coseal. e–f) Typical curves and histogram of the interfacial toughness of PAG and Coseal. g) Diagram of the burst pressure tester composed of a syringe, pressure gauge, and customized chamber. h) Burst pressures of PAGs and Coseal before and after swelling. i–j) Comparison of the burst pressures of the PAG adhesive with those of commercial bioglues (i) and other adhesives developed in related research (j). All the quantitative data are presented as the means ± s.d.s. Asterisks indicate statistically significant differences determined by ANOVA with Tukey's multiple‐comparison test as follows: *p < 0.05, **p < 0.01, and ***p < 0.001.
Cytotoxicity, hemocompatibility, and systemic toxicity of PAG. a) Live/dead fluorescence images of L929 cells cocultured with leach liquor from cured PAG (0.1 g mL⁻¹) for 1, 4, and 7 days (scale bar: 100 µm). The live cells were stained green, while the dead cells appeared red. Normal complete medium served as the control. b) Relative viability of L929 cells after culture with leachate from cured PAG (0.1 g mL⁻¹) for 1, 4, and 7 days. c) SEM images of residual blood on cocultured cured PAG, cured Coseal, glass, HDPE, and natural rubber substrates (scale bar: 5 µm). d) Quantitative analyses of (i) coagulant properties in the negative control, blank, cured PAG and cured Coseal groups; (ii) hemolytic properties in the positive control, cured PAG, and cured Coseal groups; and (iii–vi) hematological analyses of white blood cells (WBCs (iii)), red blood cells (RBCs (iv)), platelet counts (PLTs (v)), and hemoglobin (HGB (vi)) in the blank control, negative control, cured PAG, and cured Coseal groups. e–g), In vivo systemic toxicity of cured PAG and cured Coseal in mice. Untreated mice served as the blank control. Body weight changes in mice treated with different bioglue implants for 4, 24, 48, and 72 h (e). Blood smears after 72 h of treatment (f) (scale bar: 20 µm). H&E staining images of heart, liver, spleen, lung, and kidney tissues from mice treated for 72 h with different bioglue implants (g) (scale bar: 100 µm). All the quantitative data are presented as the means ± s.d.s. Asterisks indicate statistically significant differences determined by ANOVA with Tukey's multiple‐comparison test and two‐sided Student's t‐test between two groups as follows: *p < 0.05, **p < 0.01, and ***p < 0.001.
Sealant properties of PAG in a rat abdominal artery puncture model. a) Diagram of the surgical procedure used to seal the rat abdominal artery puncture using PAG. b) Fourteen‐day schedule of postoperative observation and treatment of the model rats. c) Photographs of artery punctures sealed by Coseal and PAG. d–f) Statistical evaluation of the dose (d), surgical duration (e), and postoperative survival rate of rats treated with Coseal and PAG (f). g–h) Photographs of immunostained (g) (scale bar: 100 µm) and immunohistochemically stained (h) (scale bar: 100 µm) wound sites treated with bioglues. i–j) Quantitative diagnostic pathology image analysis of the immunostaining (i) and immunohistochemical (j) results of the wound sites treated with the bioglues. All the quantitative data are presented as the means ± s.d.s. Asterisks indicate statistically significant differences determined by ANOVA with Tukey's multiple‐comparison test as follows: *p < 0.05, **p < 0.01, and ***p < 0.001.
Minimally invasive closure of the porcine femoral artery using PAG. a) Diagram of the surgical procedure for sealing the porcine femoral artery puncture using PAG. b) Twenty‐eight‐day schedule of postoperative observation and treatment of model pigs. c,d) Subcutaneous extravasated blood at the puncture site (c) and calculation of the pressing time (d) after treatment with Exoseal and PAG. The puncture site was not subjected to any treatment except for pressing served as the control. e) Diagram of the surgical procedure used to seal the porcine femoral artery puncture using Exoseal and PAG. f) Observation of the punctured artery treated with Exoseal and PAG on postoperative days 1 and 14 (scale bar: 30 mm). g–i) Histopathologic analyses of the wound sites treated with Exoseal and PAG via Masson staining (g), collagen fiber and elastic fiber (EVG) staining, (h) and Von Kossa staining (i) on postoperative day 28 (scale bar: 100 µm).
Polyurethane‐Based Bioglue for the Repair of Arterial Ruptures

Wenxuan Wu

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Chengkai Xuan

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Yaqiang Jiang

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Xuetao Shi

A bioglue with fast blood absorption and strong adhesion, capable of stopping bleeding through physical blockage rather than coagulation, is imperative for treating arterial hematorrhea during surgery and in wilderness first aid. Here, we developed a two‐component polyurethane‐based arterial glue (PAG). The key strategy of this work is to optimize the hydrophilicity and crosslinking density of the bioglue by modulating the proportion of hydrophilic polyethylene glycol (PEG)‐based urethane prepolymer, the hydrophobicamine crosslinkers, and the functionality of the crosslinkers. Compared with commercial PEG‐based bioglue, PAG has a similar water absorption rate but less swelling. Furthermore, owing to the hydrogen bonding originating from the urethane/urea bonds and extracovalent bond formation with tissue, PAG showed ≈2 times greater adhesive strength than commercial PEG‐based bioglues. In addition, PAG has good hemocompatibility and maintains cured integrity even under circulating blood flushing conditions, thereby reducing the risk of arterial embolism. This bioglue demonstrated a more reliable sealing effect with a higher survival rate compared to commercial fibrin and PEG‐based bioglues on the rat abdominal aorta and rabbit carotid artery in open operations; moreover, it can be assembled into a commercial balloon dilation catheter system, enabling minimally invasive surgeries on the porcine femoral artery.


Illustration of the fabrication and structure of s‐UCNTBs‐MoS2 heterojunction networks.
Characterizations of s‐UCNTBs and s‐UCNTBs‐MoS2 heterojunction networks. a) Schematic illustration of the experimental setup for the synthesis of s‐UCNTBs‐MoS2 networks. b) Optical micrograph and c) Raman spectrum of s‐UCNTBs‐MoS2 heterojunction networks. d) SEM and the elemental mapping images of s‐UCNTBs‐MoS2. e,f) TEM images of s‐UCNTBs and a single‐walled CNT coated with a MoS2 layer, respectively. g) HRTEM image and (h) the corresponding SAED pattern of s‐UCNTBs‐MoS2 heterojunctions. i) HAADF‐STEM image of s‐UCNTBs‐MoS2. j) HAADF‐STEM images of MoS2, the inset displays the corresponding fast Fourier transform (FFT) pattern. k) Atomic‐resolution HAADF‐STEM image of MoS2. l) Intensity profiles of the boxed areas (marked with green and red) in (k).
Photoelectric performances of the s‐UCNTBs‐MoS2 photodetector in VIS region. a) Schematic diagram of the detector based on s‐UCNTBs‐MoS2 networks. b) Ids–Vds characteristic curves of the detector under dark and light illumination. c) Photo‐response behaviors of the detector under illumination at various wavelengths with an identical power density of 10 mW cm⁻². d) Photo‐response behaviors of the detector under illumination with different power densities at 650 nm wavelength. e) Time‐dependent ΔI/I0 behavior of the detector at a power density of 248.7 mW cm⁻² (650 nm). f) The experimental and fitting photocurrent as a function of power densities at 1 V (650 nm). g) Photo‐response behaviors of the detector under different switching frequencies. h) Response speed of the detector under 650 nm light illumination. i) The stability test.
Photoelectric properties of the s‐UCNTBs‐MoS2 photodetector in NIR region and comprehensive performance evaluation. a,b) Photo‐response behaviors of the detector under illumination with different power densities at 1064 nm wavelength. c) Relative current variation, responsivity, and d) experimental and fitting photocurrent as a function of power densities at 1.0 V (1064 nm). e) Statistical distribution of the maximum ∆I/I0 values under various incident wavelengths. f) The maximum responsivities and detectivities of the detector under various incident wavelengths. g) Performance comparison between s‐UCNTBs‐MoS2 and other reported carbon‐based, MoS2‐based photodetectors.
Photoelectric mechanisms of the s‐UCNTBs‐MoS2 photodetector. a) Photoelectric sensing mechanism and (b) energy band diagram of the s‐UCNTBs‐MoS2 photodetector. c,d) Raman spectra of s‐UCNTBs‐MoS2 heterojunction compared with pristine MoS2 and pristine s‐UCNTBs, respectively.
High‐Performance Photodetectors Based on Suspended Ultralong CNTs‐MoS2 Heterojunction Networks

Kangkang Wang

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Fei Wang

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Yang Cao

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Rufan Zhang

Carbon nanotubes (CNTs) are promising candidates for photodetectors due to their excellent electrical and optical properties. However, the strong binding energy of excitons, structural defects, and short lengths of CNTs seriously limited the full utilization of the inherently extraordinary properties of CNTs in photodetector construction. Herein, a new strategy is designed for fabricating high‐performance VIS and NIR photodetectors based on suspended ultralong CNTs‐MoS2 heterojunction networks. The MoS2 layers are directly grown on suspended ultralong CNT bundles (s‐UCNTBs). The suspended and defect‐free structures of s‐UCNTBs ensure rapid heat dissipation and perfectly avoid the electron‐phonon interactions from substrates. The interfaces between s‐UCNTBs and MoS2 effectively improve the generation and transport of photogenerated carriers, thus remarkably enhancing the photodetection performance of s‐UCNTBs‐MoS2 networks. The s‐UCNTBs‐MoS2 networks‐based photodetectors exhibit a high responsivity (8.51 A W⁻¹), a high detectivity (3.74 × 10¹¹ cm Hz1/2 W⁻¹), an ultrafast response speed (30 µs/40 µs for response/decay), and a broad detection range (405–1064 nm), far outperforming the most reported carbon materials‐based photodetectors. Moreover, the s‐UCNTBs‐MoS2 photodetector exhibits good structural and performance stability after being kept in ambient conditions for more than 200 days. This work provides a reliable way to construct high‐performance CNTs‐based devices via structural design.


Self‐rectifying resistance random access memory (SR‐RRAM) for sneak‐path current suppression. (a) Diagram of the generation of the sneak‐path current in the RRAM crossbar arrays. The red line denotes the ideal current path while the black dot lines represent the sneak‐path current paths. (b) RRAM address selected under half‐bias strategy. The red RRAM cell is selected site biased by read voltage (Vr), while the bule RRAM cells are biased by half‐read voltage (Vr/2). (c) Diagram of the self‐rectifying resistive switching for the sneak‐path current suppression. (d) Diagram of self‐rectifying resistance random access memory (SR‐RRAM) crossbar arrays based on oxide semiconductor heterojunctions (OSHs). The right inset is the cross‐section structure of the Ag/HfOx/FeOx/Au SR‐RRAM. (e) Self‐rectifying resistive switching memory behaviors characterized by typical eight switching states. (f) Demonstration of the SR‐RRAM ability on the sneak‐path current suppression, showing that the 16 RRAM cells well maintain the low conductance states even surrounded by the 128 RRAM cells that are operated to the high conductance states.
Self‐rectifying switching properties. (a) The nonlinearity that is defined as the resistance ratio, yielding over 10⁴ self‐rectifying ratio. (b) Voltage sweeping speed‐dependency of self‐rectifying resistive switching memory behavior, indicating that it was modulated by the ions at interfaces. (c) Cycling endurance of the developed memristor. (d) Voltage magnitude‐dependency of self‐rectifying resistive switching memory behavior. (e) Resistance ratio between HRS and LRS that obtained at the bias voltage point of 0.35 and 2.0V and then followed by a constant reading volage of 0.35 V, respectively. (f) Multi‐conductance states obtained from the Ag/HfOx/FeOx/Au SR‐RRAM. The 65 nonvolatile separation conductance states can at least supply 6‐bit computing precision. (g) The response on the electric stimuli with pulse width of 100ns and magnitude of 0.7V, yielding a consumption of 5.46pJ. (h–k) The SR‐RRAM‐based paired‐pulse facilitation (PPF) under double pulses with different interval times, the spike‐timing‐dependent plasticity (STDP) feature, short‐term synaptic plasticity (STP) measured 300 potentiation pluses and followed by 300 reading pluses, and long‐term plasticity (LTP) under 250 potentiation pluses and then followed by 150 reading pluses after the SR‐RRAM experiencing STP operation, respectively, suggesting that the Ag/HfOx/FeOx/Au devices can simulate the synapse function for bioinspired computing. (l) Weight updates using 100 potential electrical pulses (0.7 V, 50 µs) to set the conductance from low to high levels and then followed by 100 depression electrical pulses (−0.7 V, 50 µs) to reset the conductance from high to low levels. (m) The trap assisted Frenkel‐Poole mechanism for the self‐rectifying resistive switching memory behaviors observed in the Ag/HfOx/FeOx/Au SR‐RRAM.
Self‐rectifying switching mechanism. (a–h) UV photoelectron spectroscopy (UPS) of the FeOx and HfOx film prepared by the sputtering. (a–c) Cut‐off energy, offset, and electron affinity of the FeOx switching function layer, respectively. (d) The bandgap energy of 2.37eV of the FeOx switching function layer obtained from the offset that given by the UPS and electron affinity that given by LEIPS. The conduction band minimum (CBM) and valence band maximum (VBM) for the FeOx layer are 3.67 and 6.04 eV, respectively. (e–g) Cut‐off energy, offset, and electron affinity of the HfOx switching function layer, respectively. (h) The bandgap energy of 5.01eV of the HfOx switching function layer obtained from the offset and electron affinity. The CBM and VBM for the HfOx layer are 1.65 and 6.66 eV, respectively. (i) Band structure‐based physical mechanism for the self‐rectifying resistive switching memory behaviors.
In situ observation of HR‐TEM. (a) Cross‐section HR‐TEM image of the Ag/HfOx/FeOx/Au memristor, the signed regions denote the Ag, interface of Ag/HfOx, HfOx, and FeOx, respectively. (b–e) Crystal structure analysis for the signed regions of the cross‐section HR‐TEM image. (f) In situ HR‐TEM observation for the verification of the Ag ion diffusion and migration. From 1st to 57th second, Ag electrode has not shown obvious change. The labeled region ① maintains its shape while the region ② only migrates in Ag internal itself.
SR‐RRAM hardware computing system. (a) The in‐memory computing system based on the SR‐RRAM hardware computing system composed of 32 × 32 SR‐RRAM crossbar array, STM‐32, and driving system. (b) Configuration of a 32 × 32 matrix weight mapped onto the SR‐RRAM crossbar arrays. The image features are encoded to be the vector in which the “0” and “1” respectively represented by the 0 and 0.7 V and then enters the row‐lines, and finally obtains the output current in the column‐lines. The right is the timing diagrams of row‐ and column‐line signals and the unselected column‐lines are biased by the inhibit voltages (Vinhibit). (c) Statistics of four states from the initial low conductance state to three‐intermediate high conductance states in four random matrices (w1‐w4). (d) Eight weight updates from low‐to‐high conductance states in the SR‐RRAM hardware computing system. (e,f) Full hardware implementation of the convolutional neural network (CNN) for image recognition. (g–i) Simulation of the 784 × 100 × 10 monolayer perceptron (MLP) implantation on the in‐memory processor with 10⁵ SR‐RRAM cells for the handwritten numeral recognition, showing that an accuracy overs 97% after 5‐epoch training.
Self‐Rectifying Switching Memory Based on HfOx/FeOx Semiconductor Heterostructure for Neuromorphic Computing

Haofeng Ran

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Zhijun Ren

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Jie Li

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[...]

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Guangdong Zhou

Sneak‐path current is one of the biggest barriers for large‐scale passive memristor array integration. An ideal self‐rectifying resistance random access memory (SR‐RRAM) is a desirable solution but it has not been demonstrated today for optimizing comprehensive indexes for neuromorphic computing. The HfOx/FeOx semiconductor heterojunction SR‐RRAM with a robust self‐rectifying switching behavior featured by an average rectifying ratio (≈10⁴), high resistance ratio (>10⁶), high cycling endurance (>10⁴ cycles), high computing precision (>6 bits) and synaptic plasticity such as paired‐pulse facilitation (PPF) and the spike‐timing‐dependent plasticity (STDP) for artificial intelligence recognition is developed using the unidirectional conductivity feature of p‐n junction. The electron hopping, tunneling, and blocking in this semiconductor heterojunction that is verified by the energy band mode based on UV photoelectron spectroscopy (UPS) technology and low‐energy inverse photoelectron spectroscopy (LEIPS) and in situ high resolution transmission electron microscopy (HR‐TEM) observation plays a dominant role in the self‐rectifying analog switching behaviors. This work provides energy‐band engineering for the large‐scale memristor array integration, representing a significant advancement in hardware for neuromorphic computing.


Embracing Plasticity: Unlocking the Full Potential of Flexible and Stretchable Electronics Through the Elastoplastic Behavior of Metallic Materials

Dongqi An

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Guangping Gong

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Dian Xu

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Yewang Su

Metallic materials serving as indispensable conductors critically influence the performance of flexible electronics. Conventional structural designs have restricted metallic materials to exhibiting pure elastic deformation, but recent developments have emphasized an increased significance of plastic deformation, showing great potential for new breakthroughs in developing novel flexible electronics. This review first introduces the elastoplastic behavior of metallic materials, especially those capable of withstanding remarkable plastic deformation. The main design strategies toward flexible and stretchable electronics expanding elastic deformation range are then summarized, incorporating both strain alleviation and strain delocalization. Innovative studies exploiting plasticity for enhancing device performances or achieving shape‐forming and reconfigurable electronics are further highlighted. Some perspectives on utilizing the elastoplastic behavior of metallic materials to innovate the next generation of flexible electronics are finally provided.


Encoding of strain vector using strain‐tunable quantum geometry. a) Conceptual illustration of the biological encoding scheme. Tactile receptors generate encoded bioelectrical signals conveying information about the direction and magnitude of skin deformation, corresponding to the direction and magnitude of the strain vector. This information forms the foundation for the tactile perception of the embossed character “I”. b) The distribution of the Berry curvature without strain is shown on the left, while the three images on the right depict the distributions of the Berry curvature when uniaxial strain vectors (black arrow) are applied at 0°, 45°, and 90°, respectively. c) The distribution of the Berry‐connection polarizability tensor components Gxy without strain is shown on the left, while the three images on the right depict the distributions of the Berry‐connection polarizability tensor components Gxy when uniaxial strain vectors (black arrow) are applied at 0°, 45°and 90°, respectively. The geometric quantities of electronic bands are calculated from the 2D tilted Dirac model (see Experimental Section and Figure S1, Supporting Information for details), with the purple dashed line indicating the position of the Fermi surface.
Characterization of strain‐tunable quantum geometry by nonlinear Hall signals. a) Top view of the atomic lattice of Td‐WTe2. The black arrows in the middle represent directions along the a‐axis (the direction of the applied current) and b‐axis respectively, while the orange arrows depict the direction of the in‐plane uniaxial strain vector. An optical image of a typical device is shown below, with the configuration for electrical transport measurements indicated. b,c,d) Second‐harmonic voltage signal Vxy2ω$V_{xy}^{2\omega }$ depends linearly on the square of harmonic current amplitude when different magnitudes of strain vectors are applied at 0° (b), 45° (c), and 90° (d). e,f,g) Third‐harmonic voltage signal Vxy3ω$V_{xy}^{3\omega }$ depends linearly on the cube of harmonic current amplitude when different magnitudes of strain vectors are applied at 0° (e), 45° (f), and 90° (g). The insert plot in (g) is enlarged from the gray rectangular area. h) The second‐order nonlinear Hall signals Exy2ω/Exx2$E_{xy}^{2\omega }/{{E}_{xx}}^2$ are plotted as a function of the magnitude of the strain vector applied in different directions. i) The third‐order nonlinear Hall signals Exy3ω/Exx3$E_{xy}^{3\omega }/{{E}_{xx}}^3$ are plotted as a function of the magnitude of the strain vector applied in different directions.
Encoding mechanism revealed by temperature dependence measurement. a) The second‐order nonlinear Hall signals Exy2ω/Exx2$E_{xy}^{2\omega }/{{E}_{xx}}^2$ are plotted as a function of temperature with strain vectors applied in different directions or without strain. b) The third‐order nonlinear Hall signals Exy3ω/Exx3$E_{xy}^{3\omega }/{{E}_{xx}}^3$ are plotted as a function of temperature with strain vectors applied in different directions or without strain. c) The second‐order nonlinear Hall signals Exy2ω/Exx2$E_{xy}^{2\omega }/{{E}_{xx}}^2$ are plotted as a function of the square of the longitudinal conductivity with strain vectors applied in different directions or without strain. d) The third‐order nonlinear Hall signals Exy3ω/Exx3$E_{xy}^{3\omega }/{{E}_{xx}}^3$ are plotted as a function of the square of the longitudinal conductivity with strain vectors applied in different directions or without strain. The dashed lines in (c) and (d) are linear fits to the experimental data (dots). The coefficients extracted from these fitted curves are presented in Table S1 (Supporting Information).
Proof‐of‐concept demonstration of quantum geometry encoder. a) Conceptual illustration of the skin‐inspired encoding scheme. The detected embossed character “NJU”, the corresponding strain vector distribution, and the quantum geometry encoder array are shown separately on the left side. The second‐ and third‐harmonic components of the encoded Hall signal generated by the quantum geometry encoder, implicitly contain the direction and magnitude of strain vectors. These encoded Hall signals are then decoded by the trained artificial neural network comprising two input neurons, two hidden layers, and two output neurons. The input of ANN incorporates the experimentally measured Vxy2ω$V_{xy}^{2\omega }$ and Vxy3ω$V_{xy}^{3\omega }$ from our fabricated device, while the output of ANN provides the corresponding direction and magnitude of the strain vector extracted from the encoded Hall signals. b) Strain vectors output by the ANN for verification (red dots) and their corresponding training targets (black circles). c) The 4×4 pixels detected region is enlarged from the black rectangular area in (a), containing the part of character “U” and the block's edge. The mappings of normalized voltage signals at fundamental, second‐harmonic, and third‐harmonic frequencies are displayed in the three graphs on the right side of the upper panel. In the lower panel, the distribution of strain vectors for this region is shown on the left side and the corresponding direction and magnitude of strain vector decoded by ANN are shown on the right side. d,e) Simulation results for encoding the strain vector in embossed characters “NJU” are provided through the mappings of the direction (d) and the magnitude (e).
Skin‐Inspired in‐Sensor Encoding of Strain Vector Using Tunable Quantum Geometry

Zenglin Liu

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Jingwen Shi

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Jin Cao

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[...]

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Feng Miao

Human skin provides crucial tactile feedback, allowing to skillfully perceive various objects by sensing and encoding complex deformations through multiple parameters in each tactile receptor. However, replicating this high‐dimensional tactile perception with conventional materials' electronic properties remains a daunting challenge. Here, a skin‐inspired method is presented to encode strain vectors directly within a sensor. This is achieved by leveraging the strain‐tunable quantum properties of electronic bands in the van der Waals topological semimetal Td‐WTe2. Robust and independent responses are observed from the second‐order and third‐order nonlinear Hall signals in Td‐WTe2 when subjected to variations in both the magnitude and direction of strain. Through rigorous temperature‐dependent measurements and scaling law analysis, it is established that these strain responses primarily stem from quantum geometry‐related phenomena, including the Berry curvature and Berry‐connection polarizability tensor. Furthermore, the study demonstrates that strain‐dependent nonlinear Hall signals can efficiently encode high‐dimensional strain information using a single device. This capability enables accurate and comprehensive sensing of complex strain patterns in the embossed character “NJU”. The findings highlight the promising application of topological quantum materials in advancing next‐generation, bio‐inspired flexible electronics.


Capillarity‐assisted 3D patterning of LM in a DLP‐printed hierarchical lattice matrix. a) Schematic of the 3D patterning process. b–d) Digital images of the lattice structure at various fabrication stages (top) and corresponding microscopic images of pillar surface in the horizontal cross‐section of the liquid path (bottom): b) as‐printed structure with a pixelized smooth surface, c) LMP‐deposited pillar after liquid infusion and ethanol evaporation, and d) electrically conductive LM circuit after sintering, which illuminates a green LED.
Liquid flow behaviors in DLP‐printed flexible lattices. a) Preparation of PVP@LMP/ethanol dispersion by probe sonication. b) Wettability of LM and PVP@LMP/ethanol dispersion on DLP‐printed flexible lattice matrix with A = 496 µm. c) Schematics of the lattice architectural design for DLP printing: simple cubic unit cell and NX × NY × NZ lattice matrix. d) Simulation of the capillary rise dynamics in a lattice matrix with A = 496 µm using COMSOL Multiphysics. e) Schematic illustration of the measurement of the equilibrium capillary rise height Hc. f) Time‐lapse images showing the capillary rise of PVP@LMP/ethanol dispersion in 5 × 5 × NZ lattice matrices with A = 496 µm (top) and A = 992 µm (bottom). The red arrows indicate the liquid advancing height. g) Graph of Hc for pure ethanol and PVP@LMP/ethanol as a function of time with varying A. h) Schematic illustration of the measurement of the maximum liquid confinement height Hm. i) Effect of increasing A on Hm for PVP@LMP/ethanol dispersion confined in 5 × 5 × NZ lattice matrices. j) Graph of Hc and Hm for pure ethanol and PVP@LMP/ethanol as a function of A.
Fabrication of LM‐coated flexible elastomers via immersion and injection. a) Immersion process of a DLP‐printed lattice into PVP@LMP/ethanol. b–d) 2D and 3D shapes with uniform unit cells of A = 496 µm at different fabrication stages: i) designed models for DLP printing, ii) as‐printed structures, and iii) LM‐coated structures. e) Injection of PVP@LMP/ethanol into a programmed liquid path via a syringe. f) A flexible circuit demonstrating the illumination of a green LED in i) straightened and ii) twisted configurations. The circuit consists of unit cells with A = 496 µm on a solid substrate. g) A dual‐circuit lattice matrix capable of independently controlling the on and off states of a green and a red LED. The circuits consist of unit cells with A = 496 µm, while the supporting insulating regions consist of unit cells with A = 992 µm.
Electrical and electromechanical performance of the LM‐coated lattice structures. a) Sample with LM coating applied via immersion. b) Effect of coating layers on the mass and resistance of the LM‐coated samples. c) Relative resistance changes upon compression. d) Sample with site‐specific LM coating applied via injection. e) Relative resistance changes upon uniaxial tensile loading. f) Relative resistance changes over 1000 stretching–releasing cycles. The insets show the zoomed‐in plots for cycles 201–210 and 791–800. g) Schematic of the EMI shielding mechanism. h) EMI shielding performance of the samples. The insets show the i) as‐printed, ii) LMP‐deposited, and iii) LM‐coated samples. i) Comparison of thickness‐normalized SET for 3D‐printed flexible lattice structures.
Fabrication and testing of assembly‐free wearable sensors. a,b) A wristband designed for detecting wrist bending motions and its output ∆R/R0 signals at approximately i) 0°, ii) 20°, and iii) 40° of wrist bending. c,d) A ring‐shaped wearable sensor for detecting fingertip pressing motions and its output ∆R/R0 signals at various pressing frequencies. e,f) A shoe sole with two embedded sensors for simultaneously detecting plantar impact from the forefoot and the heel during movement, and the output ∆R/R0 signals collected from placing two encapsulated sensors beneath the forefoot and the heel during walking.
Capillarity‐Assisted 3D Patterning of Liquid Metal

Ming Gao

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Xiaojiang Liu

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Jingbo Fan

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[...]

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Kun Zhou

Flexible electronics with sophisticated 3D architectures enable multidimensional functionalities and multi‐component integration, thus surpassing their 2D counterparts in soft robotics and wearable sensors. Because of its unique metallic and fluidic characteristics, liquid metal (LM) has proven to be an excellent material for fabricating flexible electronics. However, its low viscosity and high surface tension have primarily restricted LM to the creation of 2D‐patterned films on flat surfaces, significantly limiting the complexity and functionality of the resulting flexible devices. In this work, inspired by the capillary‐driven liquid flow in a hierarchical lattice matrix, a 3D patterning method is proposed for LM and extended to the fabrication of porous materials with flexible conductivity. The feasibility and versatility of the proposed method are showcased by fabricating tunable electromagnetic interference shielding materials, programmable 3D circuits, and customizable wearable sensors, highlighting its potential for promoting the development of integrated circuits and wearable electronics.


Flexible Pressure Sensor Arrays with High Sensitivity and High Density Based on Spinous Microstructures for Carved Patterns Recognition

Wenli Zhao

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Kun Li

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Zonglin Li

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[...]

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Xiaoniu Yang

Owing to the superior stimulus perception, tactile function of skin is always the desire of flexible pressure sensor array (FPSA). However, achieving sensor arrays with high sensitivity and high resolution for tactile recognition like skin still remains a challenge. In this paper, an FPSA with high sensitivity (10.50 kPa⁻¹), high density (1134.63 cm⁻²), and sufficient sensing units (4096 units) is developed, which is one of the best results up to now. The spinous microstructures, transferring from the abrasive papers, endow the sensor array with high sensitivity. Additionally, the high density array with adequate sensing units contributes to achieving high spatial resolution for identifying various surface features. This high‐performance FPSA can obtain detailed pressure distribution for complex carved patterns. With the assistance of machine learning, the FPSA can realize precise tactile recognition, 98.48% accuracy for 12 types of mahjong tiles, indicating a promising potential in an intelligent recognition system. It is worth noting that the relationship between surface microstructures and consistency is systematically investigated for the first time, which offers valuable insights for the preparation of high‐performance sensor arrays.


Synergistic Strategy toward Enhancing Photosynthesizing Reactive Oxygen Species of Covalent Organic Frameworks

December 2024

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10 Reads

Xiaoning Zhan

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Yucheng Jin

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Chen Qu

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[...]

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Jianzhuang Jiang

Photocatalytic reactive oxygen species (ROSs) plays an important role in photodynamic therapy and photochemical reactions. However, most reported photocatalysts suffer from insufficient utilization of visible light and low conversion of O2, which requires the development of higher performance catalysts toward practical applications. Herein, a series of porphyrin‐based COFs have been prepared. Comparative experimental and theoretical studies have revealed that the synergistic interaction between the two building blocks can significantly enhance the yields of ROSs by independently accomplishing photon harvesting and oxygen capture with smooth energy transfer between them. Particularly, the ¹O2 yield of 3P‐Por‐COF is increased to 1.3 and 3.4 times that of the classical PCN‐224 and porphyrin molecular aggregates. Furthermore, the TOF of 3P‐Por‐COF is as high as 271 h⁻¹ with ≈100% selectivity under red light irradiation in catalyzing thioanisole to methyl phenyl sulfoxide. The conversion and stability of degradation of toluene gas under natural light are also superior to the conventional Fenton catalytic system. The present results should contribute to the design of high‐performance frameworks‐based photocatalysts for ROSs production.


Modified Oxygen Metabolism Toward “Sunlight‐Friendly” Photodynamic Therapy

Haiyang Zhang

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Jipeng Li

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Yongqiang Li

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[...]

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Xianqun Fan

Phototoxicity poses a substantial challenge in photodynamic therapy, resulting in intolerable skin damage, visual impairment, and reduced quality of life. Current coping strategies, primarily focus on avoiding inappropriate photoactivation and developing targeted photosensitizers, have not effectively addressed this problem. Hence, this study aims to develop a “sunlight‐friendly” photodynamic therapy strategy. Here, 1‐methoxyphenazine methosulfate (MPMS) is innovatively identified as a key substance in achieving modified oxygen metabolism. MPMS demonstrates efficient catalytic shuttling under abnormal intracellular H2O2 levels, introducing a novel protective approach for oxygen metabolism and numerous life processes. By controlling MPMS administration, the switch of the photosensitizer states between “ON” (killing tumor cells) and “OFF” (safeguarding normal cells) can be achieved. This approach effectively mitigated phototoxicity and holds the potential for widespread clinical application.


a) Schematic diagram of the structure of a plant stem. b) Schematic diagram of the preparation process of ChCu. c) Schematic diagram of the thermal transport of ions within the ChCu.
SEM images: a) layer structure of Ch6Cu6, b) Ch6Cu6 and c) interlayer structure of Ch6Cu6, in the direction parallel to the ice crystal growth. The arrow indicates the direction of ice crystal growth. SEM images: d,e) Ch6Cu6 and f) the pore wall of Ch6Cu6, in the direction vertical to the ice crystal growth. g) Fourier transform infrared spectroscopy (FTIR) spectrum and h) N 1s XPS spectrum of CS and Ch6Cu6. i) Cu 2p XPS spectrum of Ch6Cu6.
SEM images: a) Ch6Cu1, b) Ch6Cu6 and c) Ch6Cu8 in the direction vertical to the ice crystal growth. SEM images: d) Ch6Cu1, e) Ch6Cu6 and f) Ch6Cu8 in the direction parallel to the ice crystal growth. The arrow indicates the direction of ice crystal growth. g) Microscopic image of Ch6Cu6 and the corresponding 2D Raman images at the four Raman shifts. h) Schematic mechanism for the formation of laminated porous structure in Ch6Cu6 via freeze‐casting.
a) Thermal voltage of Ch6Cu6. b) Thermoelectric coefficient and corresponding SEM images of DF‐Ch6Cu6, RF‐Ch6Cu6, Ch6Cu1, Ch6Cu6 and Ch6Cu8. c) Thermoelectric coefficient of ChCu with different CuCl2 and CS concentrations. d) SEM image of Ch6Cu6 with no temperature difference applied and the corresponding EDS maps of e) Cu and f) Cl. g) Concentrations of Cu²⁺ and Cl⁻ in each small piece of Ch6Cu6 from the hot to the cold end (from 1 to 6). h) EDS maps of Cl⁻ for Ch6Cu6 under a temperature gradient of ΔT = 10.0 K. The image is a collection of EDS maps performed by six points uniformly selected from the hot to the cold end on the Ch6Cu6.
a) Temperature responsiveness of Ch6Cu6. b) Thermal voltage output curves of Ch6Cu6 at different temperature gradients. c) Thermal voltage response plot of Ch6Cu6 in contact with a champagne glass filled with hot water and the corresponding d) digital image and e) thermographic image. f) The thermal voltage plot of TEG generated by body heat and the corresponding g) digital picture of TEG and the h) digital picture of the TEG collecting the body heat.
Boosting Negative Thermopower of Chitosan Hydrogel via Bio‐Inspired Anisotropic Porous Structure

Xiaohan Sun

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Miaoqian Zhang

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Haisong Qi

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[...]

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Ang Lu

Thermoelectric materials, as key materials for realizing efficient conversion of thermal and electrical energy, are crucial for renewable energy utilization and efficient energy management. However, materials with high negative thermoelectric coefficients are relatively rare. Herein, inspired by the structure and function of plant stem which is capable of blocking heavy metal ions, chitosan/CuCl2 hydrogel (ChCu) with a huge negative thermoelectric coefficient is reported. The ChCu displayed lamellar porous structure, which is constructed synergistically by freeze‐casting technique and complexation between Cu²⁺ and chitosan. In a ChCu hydrogel subjected to a temperature gradient, most of the Cu²⁺ is immobilized within the chitosan matrix by complexation, while the thermal migration of the unbound Cu²⁺ is further intercepted by the special layered porous structure. On the contrary, Cl⁻ migrates unhindered to the cold end and accumulates, which realizes selective migration and distribution of ion/counterion. As a result, ChCu exhibits a thermoelectric coefficient as high as ‐23.8 mV K⁻¹, and can respond rapidly with a thermal voltage of 4.0 mV under a small temperature difference (ΔT = 0.3 K). This work reveals the significant influence of the polymer aggregate structure on the thermal diffusion of ions, providing an innovative strategy in designating thermoelectric materials with high‐performance, high‐efficiency and environmentally friendly.


Engineered Nanochannels in MXene Heterogeneous Proton Exchange Membranes Mediated by Cellulose Nanofiber/Sodium Alginate Dual Crosslinked Networks

Liyu Zhu

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Hongbin Yang

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Ting Xu

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[...]

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Chuanling Si

2D architectures and superior physiochemical properties of MXene offer an exciting opportunity to develop a new class of polymer electrolyte membranes by controlling the stacking behavior of MXene nanosheets. However, assembling MXene nanosheets into macroscopic stable and high‐performance proton conductors is challenging. Here, a general strategy is reported for achieving stable and high‐performance MXene‐based heterogeneous proton conductors via crosslinked cellulose nanofiber/sodium alginate (CNF/SA). Through the coordination of calcium ions with 1D CNF/SA, MXene nanosheets with abundant hydrogen‐bonding networks are firmly locked into the heterogeneous polymer network, and meanwhile, the heterogeneous polymer chains are transformed from a randomly arranged state to a long‐range ordered arrangement, and such arranged polymer molecular channels collaborate with the tightly‐stacked MXene nanosheets jointly guide the stable and efficient proton conduction. Thus, the as‐built CNF/SA/MXene (CSM) composite membrane exhibits superior mechanical properties (164.7 MPa), proton conductivity (45.4 mS cm⁻¹), power density (49.5 mW cm⁻²), and low open circuit voltage (OCV) decay rate (0.4 mV h⁻¹). The design principle of 2D material anchoring through ionic‐cross‐linking and mixed‐dimensional assembly can inspire the synthesis of various ion exchange membranes for ion filtration, ion transport, ion sieving, and more.


Electrolyte Engineering of Hard Carbon for Sodium‐Ion Batteries: From Mechanism Analysis to Design Strategies

December 2024

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12 Reads

Keying Cui

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Ruilin Hou

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Haoshen Zhou

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Shaohua Guo

The hard carbon (HC) anodes with desirable electrochemical performances including high initial Coulombic efficiency, superior rate performance and long‐term cycling play an indispensable role in the practical application of sodium ion batteries (SIBs), which are closely related to the electrolytes them matched. Fully analyzing the mechanism of electrolyte engineering for HC anodes is crucial for promoting the commercialization of SIBs, but is still lacking. In this review, the correlation between physicochemical properties of the electrolyte and the electrochemical performance of HC is first summarized. And point out the crucial role of electrolyte properties, including ion conductivity, de‐solvation energy, and interface passivation ability for the Na⁺ storage in HC. Then, the formation process, composition, as well as structure of solid electrolyte interphase (SEI) on HC surface are mainly discussed, and the structure‐activity relationship of SEI is analyzed in depth. Moreover, based on the mechanism analysis, relevant electrolyte design strategies have been summarized. Finally, the challenges and future development directions of the electrolyte engineering of HC are proposed. This review is expected to provide professional theoretical guidance for the development of electrolyte and contribute to the rational design of high‐performance HC anodes, promoting the industrialization of SIBs.


The schematic illustration of quasi‐high‐entropy interphase (QHE‐SEI) design for aqueous zinc‐ion batteries. In the diagram, the top part depicts the typical SEI and the characteristics of zinc deposition, and the bottom part represents the design of QHE‐SEI by inducing multiple components and the characteristics of zinc deposition.
The basic properties and the characterizations of the solvation structure of the electrolytes. a) The Antifreeze test, the corresponding digital photographs of designed electrolytes (ZK, ZKB, ZKBT4, ZKBT3, ZKBT2.5) at room temperature (top) and −20 °C (bottom). b) Differential scanning calorimetry (DSC) curves of various electrolytes. c) Ionic conductivities of various electrolytes at different temperatures. d) The Fourier transform infrared spectroscopy (FTIR) analysis with the changes of the composition changes in the electrolytes. e) ¹H nuclear magnetic resonance (¹H NMR) with the solvents and electrolytes. f) The fitted O–H stretching vibration of ZK and ZKBT3 electrolytes and the ratios of different H‐bond of ZK and ZKBT3 electrolytes. g) Raman spectra of S = O of OTF⁻ in ZK and ZKBT3 electrolytes. h) The radial distribution function (RDF) of Zn²⁺ (left) and i) K⁺ (right) in ZKBT3 were obtained by molecular dynamic (MD) simulation. j) The snapshot of ZKBT3 in MD simulation and schematics of the first solvent sheath about Zn²⁺ (left) and K⁺ (right) in ZKBT3. (k) Desorption modes of PF6⁻, OTF⁻, TEP, and H2O on Zn (002) surface and the corresponding adsorption energies. l) LUMO energy levels of PF6⁻, OTF⁻, TEP and H2O with Zn²⁺ or K⁺.
The electrochemical performances of electrolytes at room temperatures. a) Galvanostatic Zn plating/stripping in Zn||Zn symmetrical cell using different electrolytes (ZK, ZKBT3) with a current density of 3 mA cm⁻² and areal capacity of 3 mAh cm⁻². b) The comparison of Coulombic efficiency of Zn plating/stripping in Zn||Cu batteries with ZK and ZKBT3 electrolytes at 3 mA cm⁻² and 3 mAh cm⁻². c) In‐situ optical microscope images of Zn anode during Zn plating in the ZK and ZKBT3 electrolytes at 5 mA cm⁻², scale bar, 25 µm. d) Top‐surface (top) and Cross‐section (bottom) scanning electron microscope (SEM) images of symmetrical Zn cells with the electrolyte of ZKBT3 at 3 mA cm⁻² and 3 mAh cm⁻² after 100 cycles, scale bar, 10 µm (top) and 50 µm (bottom), respectively. e) Cycling performance of Zn||PANI battery with ZK and ZKBT3 electrolytes at 500 mA g⁻¹. f) Comparison of the initial capacity, full cell cycles, Zn||Zn and Zn||Cu performances in our work with other reported results.
The characterization of the QHE‐SEI. a) The transmission electron microscope (TEM) image and b) the high‐resolution transmission electron microscope (HR‐TEM) image of the Quasi‐high‐entropy SEI after 100 cycles formed by deposited Zn on the Cu foil at 3 mA cm⁻², 3 mAh cm⁻² in Zn||ZKBT3||Cu cell. c) The content of different elements (C 1s, N 1s, O 1s, F 1s, P 2p, S 2p, K 2p, Zn 2p) with depth distribution from X‐ray photoelectron spectroscopy (XPS) data after 100 cycles with Zn||Cu cells. d) The 3D image after 100 cycles with Zn||Cu cells of ion spatial distributions from time‐of‐flight secondary ion mass spectrometry (TOF‐SIMS) depth profiles. e) Arrhenius curves and the activation energies of Rct (top) and RSEI (bottom) derived from the Nyquist plots of Zn||Zn cells with ZK and ZKBT3 electrolytes after 19 and 50 cycles. f) In situ electrochemical impedance spectrum of the PANI||Zn full cell versus different discharge/charge states at RT (left) and LT (right) in ZKBT3 electrolyte. g) Corresponding SEI resistance of different discharge/charge states with ZKBT3 at RT (top) and LT (bottom).
The electrochemical performances of AZIBs at low temperatures. a) Galvanostatic Zn plating/stripping in Zn||Zn symmetrical cell with ZK and ZKBT3 electrolytes at current density of 3 mA cm⁻² and areal capacity of 3 mAh cm⁻². b) The electrochemical performance of the Zn||PANI battery in different electrolytes at varying temperatures. c) The charging/discharging curves with the ZKBT3 electrolyte at 500 mA g⁻¹. d) Cycling performance of Zn||PANI battery with ZK and ZKBT3 electrolytes at 500 mA g⁻¹ at −20 C. e) Comparison of the full cell and Zn||Zn performances at −20 C in our work with other reported results. f) Rate performance of Zn||PANI full cells with the ZK and ZKBT3 electrolytes. g) Image of PANI||Zn pouch cell (5 × 5.5 cm²) (left) and its thermal distribution image (right). h) The cycling stability of the PANI||Zn pouch cell at the current of 10 mA. i) The corresponding charging/discharging curves of the pouch cell in h).
Construct a Quasi‐High‐Entropy Interphase for Advanced Low‐Temperature Aqueous Zinc‐Ion Battery

Feifan Li

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Wendi Luo

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Hongwei Fu

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[...]

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Bingan Lu

The advancement of aqueous zinc‐ion batteries (AZIBs) faces significant obstacles due to the typically loose and unstable solid electrolyte interphase (SEI), which fosters dendrite formation and undermines cycling performance, especially in cold environments. Here, a quasi‐high‐entropy solid electrolyte interphase (QHE‐SEI) formulated is introduced with diverse and functional inorganic compounds, achieved through the incorporation of dual salts and a blend of solvents. Shielded by the QHE‐SEI, AZIBs exhibit uniform zinc deposition and attain remarkable cycling stability, enduring for 1300 h in Zn||Zn symmetric cells under conditions of 3 mA cm⁻² and 3 mAh cm⁻² at room temperature. Furthermore, the full cell maintains over 4300 cycles at −20 °C with nearly full capacity retention. Notably, the pouch cell maintains a high capacity of ≈25 mAh across 50 cycles, even at −20 °C. This study offers a novel approach to designing a stable SEI and elevates the performance of AZIBs.


Multifunctional Cement‐Based Composite with Advanced Self‐Sensing, Electrothermal, and Electrochemical Properties

Peng Jin

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Mohammad Kohestanian

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Masoud Hasany

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[...]

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Developing multifunctional construction materials with advanced functionalities and excellent mechanical toughness remains a significant challenge within the field of civil engineering. Herein, a scalable and cost‐effective approach for fabricating versatile cement‐based composites is introduced. This is achieved by pre‐embedding a 3D‐printed conductive lattice framework (LF) into cement pastes with the incorporation of carbon black (CB). LFs contribute significantly to the flexural extension of the composite structure and when combined with CB, they substantially improve the conductivity of the matrix, enabling its self‐sensing applications. Moreover, the obtained conductivity enables the application of electrochemical deposition techniques for in situ polymerization and deposition of polypyrrole (PPy) onto the composite surface. PPy coatings further endow the cement‐based composites with excellent electrothermal and electrochemical performance. For instance, applying a direct current voltage of 18 V for 10 min results in a temperature increase exceeding 45 °C, indicating promising de‐icing capabilities. When assembled as a supercapacitor, it exhibits an outstanding energy density, reaching 61.7 µWh cm⁻² at a power density of 150 µW cm⁻² and demonstrating its potential for energy storage application in the construction sector. In conclusion, this study introduces an innovative strategy for the advancement of intelligent and multifunctional cement‐based construction materials, emphasizing the importance of multifunctionality in modern construction practices.


Improved Anchoring of Self‐Assembled Monolayer on Hydroxylated NiOx Film Surface for Efficient and Stable Inverted Perovskite Solar Cells

December 2024

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4 Reads

Jinxing He

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Guanlin Li

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Guogen Huang

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[...]

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Self‐assembled monolayers (SAMs) have significantly improved the device performance of inverted perovskite solar cells (PSCs). However, the inadequate chemical bonding affinity between SAMs and the substrate as well as the uneven SAM distribution can lead to the decrease in device performance. Herein, the study reports a bilayer NiOx hole transport layer (HTL), consisting of ultrathin NiOx buffer film prepared through atomic layer deposition (ALD‐NiOx) and spin‐coated NiOx film (Spin‐NiOx). The work function difference between the two NiOx films will facilitate the hole transfer from the ALD‐NiOx to the Spin‐NiOx in the ALD‐NiOx/Spin‐NiOx bilayer structure. These holes will undergo surface hydroxylation reactions with water molecules on the Spin‐NiOx film surface, generating additional hydroxyl groups covalently bonded to the Spin‐NiOx film, which can provide more anchoring sites for SAM molecules. Stable covalent bonds can be formed between the Spin‐NiOx film and the subsequently coated SAM film. As a result, SAM films with better coverage and molecular arrangement can be obtained. The ALD‐NiOx/Spin‐NiOx/SAM composite HTL also demonstrates superior charge transport capability and thermal stability. For small area PSCs (0.06 cm²) prepared by using the composite HTL, a champion power conversion efficiency (PCE) of 25.25% is achieved, and the device stabilities are also significantly improved.


Electrochemical grafting of copper terpyridine diazonium salts and thin film characterization. a) Coordination environment of Cu(II) atom in Cu(tpy‐Ph‐NH2)2.2ClO4 with atomic labeling. b) Unit cell crystal structure (Z = 2), coordination sphere of the metal complex (CuN6) with bond length in angstrom (Å), and color code of constitutional atoms, c) CV of 0.5 mm Cu(tpy‐ph‐NH2)2 recorded in acetonitrile at 100 mV s⁻¹ using 0.1 m tetra‐n‐butylammonium perchlorate as supporting electrolyte, d) CV of electrochemical grafting on graphite rod as working electrode in presence of 0.5 mM solution of in situ generated diazonium at 100 mV s⁻¹ up to 22 CV scans, e) Digital image of GR used for E‐Chem grafting, f) Proposed schematic Cu(tpy)2 oligomer formation on GR, g) Non‐contact mode 3D AFM image of Cu(tpy)2/GR thin film, h) Static water contact angle image of bare GR, and i) Cu(tpy)2/GR electrodes, respectively.
Electrochemical energy storage performance of Cu(tpy)2/GR electrode recorded in 0.1 m HClO4 and compared with acetonitrile and aqueous solvents. a) CV of bare GR and Cu(tpy)2/GR in 0.1 m HClO4 in acetonitrile, b) CV of bare GR and Cu(tpy)2/GR in 0.1 m aqueous HClO4 at 20 mV s⁻¹ and 50 mV s⁻¹ scan rate, c) DPV of Cu(tpy)2/GR electrode before and after methylation of free pyridine unit, d) Capacitance for bare GR and Cu(tpy)2/GR electrodes calculated at 10 mV s⁻¹, e) CV showing Faradaic capacitive contribution (pink shades) and Faradaic non‐capacitive contribution (white shades) estimated using the Dunn method, and f) Faradaic and diffusive capacitive contribution for Cu(tpy)2/GR at different scan rates.
Galvanostatic and AC‐based electrochemical measurements for Cu(tpy)2/GR electrodes. a) GCD cycle of bare GR, b) Cu(tpy)2/GR in 0.1 m aqueous HClO4 electrolyte at a current density of 0.5 mA cm⁻², c) GCD cycling of Cu(tpy)2/GR at different current densities, d) respective capacitance value, e) cyclic stability of bare GR and Cu(tpy)2/GR at 0.8 mA cm⁻², f) capacitance retention (left vs bottom) and Coulombic efficiency (right vs bottom) plot of Cu(tpy)2/GR electrode at 0.8 mA cm⁻², g) Nyquist plot, and h) Bode plot of Cu(tpy)2/GR in 0.1 m aqueous HClO4 at 0 V versus Ag/AgCl in the frequency range 0.1 Hz to 10⁴ Hz with 5 mV amplitude, and i) equivalent circuit used to fit the experimental data.
DFT optimized possible structures for Cu(tpy)2 on the graphite rod. a‐f) DFT optimized possible structures for the dimeric complexes formed. The green shape shows the presence of Cu(II) with an octahedral geometry, whereas the blue shape shows Cu(I) with a tetrahedral geometry. The yellow regions show the point of attachment to the ZGNR. g) spin density of the pristine complex Cu(II)‐Cu(I)‐(C─C). h) charge difference density of the Cu(II)‐Cu(I)‐(C─C) chemisorbed on graphene sheet showing significant interaction with graphene sheet. i) Total density of states for Cu(II)‐Cu (I) complex@ZGNR and the projected density of States corresponding to ZGNR and Cu(II)‐Cu(I) complex.
Plausible charge storage mechanism of Cu(tpy)2/GR electrode. a) HOMO (bottom) and LUMO (top) distribution for Cu(II)‐Cu(I)/GR cluster (isovalue: 0.02). b) Partial quare scheme for PCET in the Cu(II)‐Cu(I)/C48‐cluster. The starting species, having the distal Cu center with a (+II) oxidation state and the graphitic flake partially oxidized, displays no net unpaired spin density. Upon the addition of one electron, the distal Cu site is reduced, and the unpaired electron is mainly distributed over the graphitic layer, which remains almost unchanged upon subsequent protonation. Isovalue: 0.002.
Unlocking the Potential of Redox‐Active Copper Complexes in Thin Films via Proton‐Coupled Electron Transfer for Enhanced Supercapacitor Performance

Ritu Gupta

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Ankur Malik

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Pradeep Sachan

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[...]

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Nanoscale redox‐active molecular films are promising candidates for next‐generation energy storage applications due to their ability to facilitate long‐range charge transport. However, establishing stable and efficient electrode‐molecule interfaces remains a critical challenge. In this study, the properties of redox‐active copper‐polypyridyl thin films covalently bonded to graphite rods are explored, investigating their potential as supercapacitors. Using an electrochemical grafting method, robust covalent interfaces are created, resulting in copper‐polypyridyl films prepared on graphite rods and indium tin oxide (ITO) electrodes, exhibiting both Cu(II) and Cu(I) redox states. These redox‐active mettalo‐oligomeric films demonstrate a structural transition between octahedral and tetrahedral geometries around the Cu(II), and Cu(I), respectively contributing to their charge storage capabilities. The combination of an electrical double‐layer capacitance and pseudocapacitance through Faradaic charge transfer is evaluated in different acidic electrolytes, showing significant capacitance enhancement. Notably, proton‐coupled electron transfer (PCET) at free pyridine‐N sites in Cu(I) polypyridyl complex is identified as a key factor in their distinct behavior in aqueous solutions, a finding supported by computational studies. This study shows the potential of binder‐free thin films for efficient supercapacitor applications, with a maximum areal capacitance of 6.8 mF cm⁻² in aqueous media, representing an 1840% improvement over bare graphite rods.


Synergistic Effect of Surface States and Deep Defects for Ultrahigh Gain Deep‐Ultraviolet Photodetector with Low‐Voltage Operation

December 2024

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10 Reads

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Kongping Wu

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·

[...]

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To achieve ultra‐high gain deep‐ultraviolet (DUV) detectors based on ultra‐wide bandgap semiconductors comparable with those of bulky photomultiplier tubes (PMTs), avalanche photodiodes have usually been adopted. However, the high‐operation voltage (∼100 V) is not compatible with monolithic integration. Herein, it is demonstrated that the ultra‐high gain DUV photodetectors (PDs) with low operation voltages (<5 V) can be achieved by using the synergistic effect of surface states and deep defects in a type‐Ib single‐crystal diamond (SCD) substrate. The overall photoresponse, such as the sensitivity, dark current, spectral selectivity, and response speed, of the diamond DUV‐PDs can be simply tailored by the surface hydrogen or oxygen termination of the SCD substrate. The DUV responsivity and external quantum efficiency are more than 2.5 × 10⁴A/W and 1.4 × 10⁷%, respectively, at 220 nm‐wavelength light, comparable with those of PMTs. The DUV/visible light rejection ratio (R220 nm/R400 nm) is as high as 6.7 × 10⁵. The depletion of the 2D hole gas by deep nitrogen defect provides a low dark current and the filling of the ionized nitrogen upon DUV illumination induces a huge photocurrent. The synergistic effect of the surface states and the bulk deep defects opens the avenue for the development of DUV detectors compatible with integrated circuits.


Artificial Intelligence in Metamaterial Informatics for Sonic Frequency Mechanical Identification Tags

December 2024

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23 Reads

Daniel Saatchi

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Myung‐Joon Lee

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Tushar Prashant Pandit

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[...]

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Il‐Kwon Oh

Designing mechanical metamaterials to control wave propagation often requires extensive finite element analysis and discrete Fourier transform simulations before fabricating 3D printed structures and conducting experiments. Here, an alternative approach is presented to developing a metamaterial informatics framework by integrating dataset collection with artificial intelligence (AI), which can significantly accelerate the advancement of phononic wave chip technologies based on the triply periodic minimal surface (TPMS). Visualized data analysis is performed to evaluate the sensitivity of phononic band frequency numbers (BNF). Subsequently, various machine learning algorithms are compared for the prediction of sonic BNFs to create a unique identificable encoded mechanical identification tag (EMIT) interacting with sound waves. Then, for the mechanical decoding part with the help of acoustic analogy, a novel concept technology is developed that integrates 3D‐printed EMITs with a deep‐learning audio classifier for the ownership identification of instruments. Underwater application is discussed further for civil accident investigations, such as echolocating missing aircraft, divers, sunken ships, and containers with valuable cargo. These TPMS‐based EMITs represent the first‐generation passive sonic frequency identification (SFID) transponder‐tags, marking the advent of SFID transponder systems.


Design, Fabrication, and Wearable Medical Application of a High‐Resolution Flexible Capacitive Temperature Sensor Based on the Thermotropic Phase Transition Composites of PEO/PVDF‐HFP/H3PO4

Ruohai Hu

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Ping Liu

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Wei Zhu

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[...]

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Ying Huang

Phase transition materials have the potential to be utilized as high‐resolution temperature‐sensitive materials. However, it is a challenge to develop them into temperature sensors with good stability and repeatability. In this work, inspired by phase transition theory and the electrical double‐layer capacitance principle, a novel high‐resolution flexible capacitive temperature sensor based on Polyethylene oxide(PEO)/Poly(vinylidene fluoride‐co‐hexafluoropropylene)/H3PO4 is proposed for the first time. By blending high and low molecular weight PEO and adding ionic solution, the proposed sensor exhibits high resolution (0.05 °C) and response speed (<12 s) within 35–43 °C. The novel introduction of a mesh structure aids the material in achieving microdomain control of PEO crystallization and improves the repeatability (Ex < 2.2%) of the sensor. The sensor is used for monitoring human body temperature and diabetic foot ulcers, and the results show that the sensor can achieve continuous and comfortable body temperature monitoring and early‐stage diabetic foot ulcer diagnosis, offering broad applications in health monitoring and rehabilitation medicine.


The Future of Nanomaterials Tackling the Challenge of Delivering Nucleic Acids to the Retina

December 2024

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11 Reads

José Hurst

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Friederike Adams

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Sven Schnichels

Ocular gene therapy targets eye diseases at the genetic level. Systemic transport of nucleic acids to ocular tissues poses a significant challenge, as the effectiveness of crossing the blood‐retina barrier limits nucleic acid penetration. Therefore, local administration, such as topical, periocular, or intraocular, can improve the outcome of in vivo gene therapy by bypassing the first‐pass effect and minimizing the systemic toxic effects. The eye is an immune‐privileged organ with limited local immune response, making it an ideal candidate for local gene therapy. Ocular gene therapy offers a promising solution for the treatment of a wide range of retinal diseases including age‐related macular degeneration, diabetic retinopathy, retinitis pigmentosa, and Leber congenital amaurosis. Gene therapy enables replacement of mutated genes essential for visual function, delivery of genes expressing neurotrophic factors and anti‐apoptosis factors for retinal degeneration, and delivery of genes expressing anti‐angiogenic proteins for ocular neovascularization. This perspective discusses the potential of nanoparticles for nucleic acid delivery to the retina, explores challenges, and evaluates different delivery methods, including non‐viral agents such as liposomes and polymers. These nonviral agents present advantages over traditional viral vectors, showing promise in overcoming limitations and offering a viable option for retinal gene therapy.


Engineering of Nanofibers Embedded with Targeted Nanoparticles Breaks Redox Levers for Glioblastoma Therapy

Yuan Ma

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Mengqi Li

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Xiao Fu

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[...]

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Jiwei Cui

Glioblastoma multiforme (GBM), one of the most aggressive brain cancers, presents substantial therapeutic challenges, particularly concerning postsurgical recurrence and inherent drug resistance. In this study, a nanofiber‐based drug delivery system integrating platinum pro‐drugs and hemoglobin into mesoporous silica nanoparticles (HB/HSPt@MS NPs) is reported, which are surface‐modified with poly(ethylene glycol) (PEG) and targeting molecules, and subsequently embedded into nanofibers using an electrostatic spinning approach. Applied to the tumor site, these nanofibers leverage folate receptor overexpression on the tumor and the tumor's redox state to enable precise platinum release, inducing cell death through a targeted drug resistance pathway. The incorporation of hemoglobin is crucial as it disrupts the redox balance within GBM cells by facilitating the influx of iron ions, leading to lipid peroxidation through the Fenton reaction. This induces oxidative stress and overwhelms the cellular antioxidant mechanisms. This dual mechanism of action—direct cytotoxicity through sustained drug release and indirect cytotoxicity through induced oxidative stress—enhances the therapeutic efficacy of platinum drugs. The system effectively bypasses the blood‐brain barrier and reduces systemic toxicity, significantly improving delivery efficacy. Both in vitro and in vivo evaluations demonstrate substantial inhibition of tumor growth and recurrence, highlighting the potential for personalized GBM therapy.


a–d) Statistical distribution of performance parameters of S‐ref, S‐Li, S‐Ag, S‐LiAg cells. e) J–V curves of S‐ref, S‐Li, S‐Ag, S‐LiAg champion cells. f) Comparison of the FF of the state‐of‐the‐art works published in recent years.
a) Intensity‐dependent VOC and resulting approximation of the ideality factor. b) The UV–vis absorption spectrum and the band gap (Eg) are derived from the Tauc formula. c) The comparison diagram of S‐Q limit FF, pseudo‐FF (pFF), and actual FF. d) The specific value numerical histogram of FF losses attributed to non‐radiative recombination and the carrier transport of the cells.
a) The carrier concentration and mobility. b) The surface SEM images of the cells. c) XRD results of the S‐ref, S‐Li, S‐Ag, and S‐LiAg films. d) The thickness change and conductivity (σ) change of each absorption layer and the transmission resistance (Rtr). e) The cross‐sectional images of the cells. f) The comparison of the actual VOC and the VOC increase caused by the change in carrier concentration.
The UPS spectra and band arrangement schematic for CdS and a) S‐ref, b) S‐Li, c) S‐Ag, and d) S‐LiAg heterojunction interface.
a) EQE curves, b) Eu calculated from the EQE spectra, and c) Raman spectra of the S‐ref, S‐Li, S‐Ag, and S‐LiAg devices. d, e) The area ratio maps of the 174 and 234 diffraction peaks to the main peak. f) C‐V and DLCP curves under 1 kHz, g) DLCP curves at 1 and 200 kHz, and h, i) TPV, TPC curves and the decay lifetime (τTPV and τTPC) of the S‐ref, S‐Li, S‐Ag, and S‐LiAg devices.
Li, Ag Co‐Doping Enables Efficient Kesterite Solar Cell with a High Fill Factor of 74.30%

Xinyi Zhong

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Jinlin Wang

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Litao Han

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[...]

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Sixin Wu

In addition to open‐circuit voltage (VOC) loss, fill factor (FF) loss is considered another major factor restricting the further optimization of Cu2ZnSn(S,Se)4 (CZTSSe) device efficiency. In this work, a comprehensive investigation into the loss mechanisms of FF has been conducted, and implemented a Li&Ag co‐doping approach to enhance FF. The results indicate that the FF loss caused by insufficient carrier extraction is higher than that caused by non‐radiative recombination. The carrier extraction capability is significantly influenced by the band alignment of the CdS/CZTSSe interface and has little relationship with the carrier concentration of the absorber. Therefore, although Ag doping reduces the hole concentration and conductivity, it reduces the FF loss caused by carrier extraction due to the improvement of band alignment. Ag doping is also superior to Li in passivating harmful defects, which helps reduce FF losses caused by non‐radiative recombination. Correspondingly, Li performs better than Ag in increasing the hole carrier concentration and optimizing band alignment, greatly reducing FF losses caused by insufficient carrier transport. Finally, the Li and Ag co‐doping strategy enables a 14.91% efficient kesterite solar cell with the highest reported FF to date of 74.30% through collaborative optimization of carrier extraction and suppression of non‐radiative recombination.


Bias‐Free Photoelectrochemical Water Oxidation Coupled with Electrochemical Oxygen Reduction Reaction via Fe‐Based Electrodes with Long‐Term Operation

December 2024

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19 Reads

Photoelectrochemistry (PEC) is a green and sustainable approach in the synthesis of H2O2, depending on the semiconductor to initiate two‐electron water oxidation into hydrogen peroxide (H2O2). However, the photoanodes generally have sluggish charge transfer and a limited number of active sites, which limit the yield and faradaic efficiency (FE) for the production of H2O2. Herein, Ti‐doped Fe2O3 photoanode with the modification of ZnO passivation layer (ZnO/Ti‐Fe2O3) for PEC H2O2 production is developed. The optimized photoanode has shown a high FE and selectivity for two‐electron water oxidation, achieving a yield approaching 0.56 µmol min⁻¹ cm⁻² at 1.23 VRHE and an average FE over 80% in the potential range from 1.0 to 1.6 VRHE. Impressively, an unassisted PEC system is designed to generate H2O2 at the ZnO/Ti‐Fe2O3 photoanode while performing an oxygen reduction reaction (ORR) at the Fe(Co)‐NC cathode. The integrated system enables the average PEC H2O2 production rate of 0.275 µmol min⁻¹ cm⁻² without applying any additional bias. Moreover, an unassisted PEC cell obtains a long‐term stability of 100 h. This work demonstrates new possibilities in designing efficient and stable PEC assemblies using low‐cost earth‐abundant materials for light‐driven catalysis.


Engineering the Microstructure and Spatial Bioactivity of MAP Scaffolds Instructs Vasculogenesis In Vitro and Modifies Vessel Formation In Vivo

Alexa R. Anderson

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Eleanor L. P. Caston

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Lindsay Riley

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[...]

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Tatiana Segura

In tissues where the vasculature is either lacking or abnormal, biomaterials can be designed to promote vessel formation and enhance tissue repair. In this work, the microstructure and bioactivity of microporous annealed particle (MAP) scaffolds are independently tuned to guide cell growth in 3D and promote de novo assembly of endothelial progenitor‐like cells into vessels. Both in silico characterization and in vitro experimentation are implemented to elucidate an optimal scaffold formulation for vasculogenesis. It is determined that MAP scaffolds with pore volumes on the same order of magnitude as cells facilitate cell growth and vacuole formation. Spatial control over cell spreading is achieved by incorporating adhesive microgels in well‐mixed, heterogeneous MAP scaffolds. While it is demonstrated that integrin engagement is the primary driver of network formation in these materials, introducing adhesive microgels loaded with heparin nanoparticles leads to the formation of vascular tubes after 3 days in culture. It is then shown in vivo that this unique scaffold formulation enhances vessel maturation in a wound‐healing model and instructs differential vascular development in the tumor microenvironment. Taken together, this work determines the optimal microstructure and ligand presentation within MAP scaffolds that leads to vascular constructs in vitro and facilitates vessel formation in vivo.


Journal metrics


18.5 (2023)

Journal Impact Factor™


21%

Acceptance rate


29.5 (2023)

CiteScore™


13 days

Submission to first decision


$5,510 / £4,160 / €4,810

Article processing charge

Editors