Research ArticleAPPLIED PHYSICS

Gate-controlled VO2 phase transition for high-performance smart windows

See allHide authors and affiliations

Science Advances  15 Mar 2019:
Vol. 5, no. 3, eaav6815
DOI: 10.1126/sciadv.aav6815

Abstract

Vanadium dioxide (VO2) is a promising material for developing energy-saving “smart windows,” owing to its infrared thermochromism induced by metal-insulator transition (MIT). However, its practical application is greatly limited by its relatively high critical temperature (~68°C), low luminous transmittance (<60%), and poor solar energy regulation ability (<15%). Here, we developed a reversible and nonvolatile electric field control of the MIT of a monoclinic VO2 film. With a solid electrolyte layer assisting gating treatment, we modulated the insertion/extraction of hydrogen into/from the VO2 lattice at room temperature, causing tristate phase transitions that enable control of light transmittance. The dramatic increase in visible/infrared transmittance due to the phase transition from the metallic (lightly H-doped) to the insulating (heavily H-doped) phase results in an increased solar energy regulation ability up to 26.5%, while maintaining 70.8% visible luminous transmittance. These results break all previous records and exceed the theoretical limit for traditional VO2 smart windows, making them ready for energy-saving utilization.

INTRODUCTION

Designing improved energy-saving materials is an active research topic in materials science because of the increasing concerns related to energy consumption and sustainable development. It is known that residential buildings are responsible for almost 30 to 40% of the primary energy consumption in the world (1). Thus, the use of chromogenic materials on building fenestration and the applications of building-integrated photovoltaic technologies such as solar cells have been demonstrated to be effective ways to increase the energy efficiency of buildings and reduce the energy consumption (27). Notably, smart coatings based on thermochromic materials, the so-called “smart windows,” can modulate the transmittance of solar radiation in response to the change of temperature, making them very promising for improving the energy utilization efficiency of buildings (8).

As a typical thermochromic material, vanadium dioxide (VO2) has been widely investigated because of its pronounced metal-insulator transition (MIT) behavior at the critical temperature of 68°C (911). During the MIT process, VO2 shows a sharp change of resistance and a pronounced optical switching behavior especially in the infrared region, which makes it promising for energy-efficient coating applications (1221). However, obstacles including high transition temperature at ~68°C, low luminous transmittance (Tlum < 60%), and weak solar energy regulation ability (ΔTsol, usually <15%), make the VO2-based smart window still far from practical (2224).

In this study, we developed an electrochromic smart window system based on a VO2 film with gate voltage control via a solid electrolyte. By adding gating voltage to control the H-doping level, we tuned nondestructive and reversible phase transformations between the insulating pristine monoclinic VO2, metallic HxVO2 (0 < x < 1), and insulating HVO2 phases at room temperature. Synchrotron-based spectroscopies were used to identify the crystal structures, electronic states, and the orbital occupancies during these field-controlled phase transitions. By analyzing the optical transmission properties of this system, we have demonstrated that the solar energy regulation ability is greatly augmented (ΔTsol ~ 26.5%), via the transition between the metallic HxVO2 (0 < x < 1) phase, which can block most infrared transmissions, and the insulating HVO2 substantially, which has a high visible luminous transmittance (Tlum up to ~70.8%). This not only substantially surpasses the performance of systems reported previously but also exceeds the theoretical limit of ΔTsol ~ 23% for a pure VO2 material. Thus, the current results will provide a promising basis for the development of practical energy-saving devices in the future.

RESULTS

Gating-induced reversible three-phase transitions for VO2 films

An electric field applied with ion liquid (IL) gating is effective in modulating the properties of metal oxide materials. Recent reports showed that gating voltage with water-involved IL could induce the insertion/extraction of either oxygen anions or hydrogen cations into/from some oxides, implying phase modulation through electric field control (2530). Here, we adopted a gel-like solid electrolyte [NaClO4 dissolved in polyethylene oxide (PEO) matrix; see Materials and Methods] as the gating layer (Fig. 1, A and B). The solid electrolyte covered both the prepared 30-nm VO2/Al2O3(0001) thin film and the three gold electrodes. In addition, the source and drain electrodes had good contact with the VO2 thin film, realizing a typical field-effect transistor (FET) configuration. Positive or negative voltages applied through the gating electrode could drive the insertion/extraction of hydrogen ions into/from the VO2 lattice (2931), resulting in the stabilization of the metallic VO2 phase at room temperature due to hydrogen insertion.

Fig. 1 Experimental schemes.

(A) The gating diagram of the VO2 device with source, drain, and gate electrodes. (B) Hydrogen ion movement under gating control. (C) The reversible insulator-metal-insulator tristate phase transitions of VO2 by tuning hydrogenating level with positive (blue) or negative (red) gating voltages.

Hydrogen doping in the VO2 crystal was frequently studied under the high-temperature annealing treatment assisted by a noble metal catalyst in H2 gas (3234), which could also lead to the formation of a metallic H-doped VO2 state. Conversely, as reported recently by Yoon et al. (35) and our group (36), catalyst-assisted high-temperature annealing can produce another insulating HVO2 phase. Thus, is it possible to realize the tristate phase transitions as shown in Fig. 1C by the gating treatment at room temperature?

As expected, phase transitions are found to be strongly dependent on the gating voltage. Figure 2A shows the changes in electrical resistance under gating voltages of 1.0 and 2.0 V, respectively, as a monitor of the phase transitions between insulator and metallic states (see the laboratory-scale gating device in fig. S1A). At a gating voltage of 1.0 V, the film resistance gradually decreases from ~106 to ~103 ohms even after 400 min (red curve), indicating a transition from an insulator to a metallic state. Upon the application of a gating voltage of 2.0 V (green curve), the film resistance first decreases from ~106 to ~3 × 103 ohms after about 25 min and then gradually increases up to ~2 × 105 ohms, indicating a transition from an insulator to a metallic state, and then back to an insulator state. This gating process is also sensitive to sample temperature (see fig. S1B): The higher the temperature, the quicker the gating-induced phase changes appear. For example, at 60°C, the gating-induced phase transition can be finished within several minutes, which demonstrates the potential for fast switching during practical applications. Figure 2B shows the x-ray diffraction (XRD) measurements for the pristine VO2 film and the samples gated by 1.0- or 2.0-V gating for 300 min, respectively. In contrast to the 39.8° XRD peak of the VO2 (020) diffraction for the nongated pristine sample, peaks at 39.4° and 36.8° are assigned to the gating-induced metallic film and the insulating sample by 1.0 and 2.0 V, respectively (36). One can also monitor the varying of XRD signals (Fig. 2C) to understand the gradual evolution of crystal structures during the gating cycles. It is observed that the reversible phase modulations are made by adjusting voltages as a function of gating time (Fig. 2D). Starting from the pristine VO2 structure, the original insulating sample is first transformed to the metallic phase by a gating voltage of 1.0 or 1.5 V. A new insulating phase is formed when the gating voltage is increased to 2.0 V. Then, upon the addition of a negative voltage of −1.0 V, the insulating VO2 is gradually converted to the metallic phase. The initial monoclinic VO2 phase is recovered by further increasing the negative voltage to −2.0 V.

Fig. 2 Phase modulation by the gating treatment.

(A) The resistance changes as a function of gating time at gating voltages of 1.0 V (red) or 2.0 V (green). (B) XRD curves for the pristine VO2 film (black) and for VO2 films subjected to gating voltages of 1.0 V (red) or 2.0 V (green) for 300 min. a.u., arbitrary units. (C) XRD curves for VO2 films treated with different gating voltages. To monitor the intermediate states, the gating time was set to 60 min for voltages of 1.0 and −2.0 V, while it was set to 60 and 120 min for voltages of 1.5, 2.0, and −1.0 V. (D) The reversible phase modulations by different voltages as a function of gating time. (E) A cycling resistance test plot produced by sweeping the gating voltage from −2.0 to 2.0 V at a sweep rate of 0.4 mV/s and a source-drain voltage of 0.3 V, indicating a series of reversible phase transitions between the insulating monoclinic M-VO2 state (starting from point A) and the metallic HxVO2 state. (F) A cycling resistance test plot at a slower sweep rate of 0.1 mV/s and a source-drain voltage of 0.3 V, indicating a series of reversible phase transitions between three states: the initial monoclinic insulator M-VO2 state (point A), the metallic HxVO2 state (point B), and the insulating HVO2 state (point C). Arrows indicate the direction of resistance changes during voltage sweeping.

Loop tests were conducted by keeping the source-drain voltage of 0.3 V while sweeping the gating voltage at either a fast or a slow rate. Under the fast sweeping mode with a rate of 0.4 mV/s (Fig. 2E), the film resistance gradually decreased from ~106 to ~103 ohms as the gating voltage increased from 0.0 to 2.0 V (starting from point A), indicating a transition from an insulator to a metallic state. If the voltage decreased from 2.0 to −2.0 V, the metallic state (~103 ohms) was maintained, but once the negative gating voltage reached a threshold value, it completely changed to an insulator state (~106 ohms). Thus, during the fast-rate loop test, a simple and reversible transition between the insulator M-VO2 and the metallic HxVO2 state was observed. Conversely, when applying the gating voltage at a slower sweeping rate of 0.1 mV/s, a quite different variation contour involving tristate phase transitions was obtained (Fig. 2F). Along the positive gating direction, the film was transformed from the initial M-VO2 state (point A) to the metallic HxVO2 state (point B), and then higher positive voltage led to another insulating HVO2 state (point C). Thereafter, as the gating voltage decreased toward −2.0 V, the insulating HVO2 phase was first changed back to the metallic state and then eventually reverted to the initial insulating M-VO2 state, finishing a full cycle. This transition loop was ascribed to the sequential insulator-metal-insulator tristate phase transitions. This was consistent with the resistance varying as a function of gating time in Fig. 2A, as the 2.0-V gating treatment gradually turned the pristine structure to the metallic state and later to the insulating phase. Accordingly, for gating treatment, both the gating voltage and gating time were key factors for phase modulation as they are the primary determinants of the degree of hydrogen insertion and diffusion into the VO2 lattice.

Gating-induced hydrogen doping in VO2 films

We then performed additional experiments to identify the varying of the VO2 crystal structure along with gating treatment. By gating with positive voltage, the cations will be driven into the VO2 lattice. Since the radius of Na+ (~0.102 nm) is a bit larger than that of V4+ (~0.058 nm), it is quite difficult to insert Na+ in the electrolyte into the VO2 lattice or for it to replace other cations there. The detailed x-ray photoelectron spectroscopy (XPS) test (see fig. S2) validates the situation, while secondary ion mass spectrometry (SIMS) tests (see fig. S3) reveal that the metallic and insulating phases induced by positive gating hold increased hydrogen concentrations.

The mechanism of hydrogen doping into the VO2 lattice by gating treatment basically involves the migration of hydrogen driven by the electric field, which is analogous to the charging and discharging process in a Li+ battery or the catalyst-free hydrogenation of VO2 in acid solution (37). The chemical reaction for the hydrogenation can be described asVO2+x(H+)+(x e)HxVO2(0<x1,eis an electron)(1)

In this process, (H+) migrates into VO2 from the electrolyte driven by the positive gating voltage, and the electron is provided through the gating circuit. For the restoration process, the chemical reaction isHxVO2VO2+x(H+)+(x e)(2)

Protons will migrate into the electrolyte from the VO2 lattice because of the negative gating voltage.

For this gating treatment, the source of protons in the electrolyte should be considered (2527, 30). Our gating experiment shows that 1.0-V gating voltage can induce the metallic H-doped VO2 film. As this voltage is less than the 1.23 V required for electrolysis of water, the adsorbed water in the electrolyte layer is unlikely to be the source of protons. Residual methanol in the electrolyte (see fig. S4) might be the possible source of protons because of its lower electrolysis voltage, although further chemical or electrochemical studies are required to confirm it.

In addition, it was also observed that these H-doped VO2 films were quite stable in air (see fig. S5), which demonstrated the nonvolatile property of the electric field control phase transitions under ambient conditions. Raman tests (see fig. S6) on gated samples suggested that the hydrogenated VO2 film showed a rutile-like phase structure since the characteristic peaks at 192, 223, and 617 cm−1 in pristine monoclinic VO2 were completely absent. These phase structures were sensitive to the H-doping concentration, providing further validation that hydrogen ions are being inserted into the VO2 lattice.

Detailed synchrotron-based XPS and x-ray absorption near-edge spectroscopy (XANES) in Fig. 3 show that pronounced peaks due to the presence of –OH emerge in the metallic phase after gating treatment at 1.0 to 1.5 V. In addition, the peak becomes much stronger with higher voltage and longer treatment time (Fig. 3A), reflecting a higher H-doping concentration in the newly formed insulating state. Specifically, the V2p3/2 peaks in the XPS curves become broader and slightly shift toward the low binding energy direction after gating treatment, indicating the appearance of a small amount of V3+ state due to the charge transfer induced by H atoms (38). Synchrotron-based XANES for V L-edge in Fig. 3B confirms the electronic structure variations induced by H-doping during the gating treatment. The V LIII-edge undergoes a pronounced shift to lower energy after gating, indicating that the V atoms are in a lower valence state (39, 40). The O K-edges in Fig. 3C show the transitions from O1s to O2p states, in which two distinct features of the t2g and eg peaks reflect the unoccupied states. The intensity ratio of t2g/eg decreased substantially with the gating treatment, which is caused by the increased H-doping concentration and reflects the fact that t2g levels including the d//* and π* orbitals are gradually filled by electrons.

Fig. 3 Chemical and electronic states of gating-treated VO2 films.

(A) XPS curves of VO2 films with different gating voltages. (B) V L-edge XANES curves and (C) O K-edge curves for the samples gated at 2.0 V with different gating times.

Theoretical simulations for the gating effects

First-principles calculations at the density functional theory (DFT) level were carried out to explore the underlying microscopic mechanism of the gating effects. The formation energies of H-doping and H-diffusion energy barrier were computed using supercells containing different H concentrations: V4O8, HV4O8, and H2V4O8 (Fig. 4, A to C). The formation energy of H-doping impurity is near −3.6 eV, which is insensitive to H concentrations (see table S1). This is because all H impurities are stabilized at the center of lattice vacancy, forming relatively strong H─O bonds, as shown in Fig. 4 (B and C) (see also fig. S7). In contrast, the H-diffusion energy barrier becomes increasingly larger with the increase in H-doping concentration. In VO2, the channels for H diffusion are mainly along the [100] direction because there are no V atoms or O atoms to hinder the diffusion (Fig. 4A). The calculated H-diffusion energy barrier value is 0.8 eV along the [100] direction (Fig. 4D). Conversely, the diffusion barriers in HV4O8 and H2V4O8 were increased to 1.15 eV (Fig. 4E) and 1.38 eV (Fig. 4F), respectively. This increase is due to blockage of the channels for H diffusion by the intercalation of H atoms. Moreover, the geometric variations induced by initial H-doping may also hinder the diffusion of successive H atoms. This H-dependent barrier increase explains our experimental finding that a high gating voltage of 2.0 V was required to induce the large H-doping concentration required to generate the insulation phase of the H-doped VO2 film.

Fig. 4 Theoretical calculation for H insertion and diffusion processes.

(A to C) Optimized atomic structures of V4O8 (pure VO2), HV4O8, and H2V4O8, respectively. Purple beads with arrows represent H-diffusion channels along the [100] direction. (D to F) Calculated energy barriers for diffusion of H atoms into V4O8, HV4O8, and H2V4O8, respectively.

Gate-controlled VO2-based smart window with high performance

The smart window concept was proposed many years ago, and many materials showed promise for use as smart windows, including hydrogels, liquid crystals, transition metal oxides, and perovskite (41, 42), because of their special optical response in the visible region upon external stimulus/excitation. The VO2 material exhibited a special switching effect in the near-infrared (NIR) range across the phase transition, which demonstrated a unique advantage in energy-saving applications. Since the phase transformations of VO2 films can be controlled by gating treatment at room temperature, we were able to apply it to a voltage-controlled smart window, as shown schematically in Fig. 5A. For the VO2 films with three different phase structures, obvious color changes were observed. The pure VO2 film and the gating-produced metallic HxVO2 film showed a similar yellowish color, while the heavily H-doped VO2 film was almost transparent. In Fig. 5B, the metallic HxVO2 film showed transmittance spectra similar to those of the rutile VO2 film (VO2 film at 90°C), demonstrating a pronounced switching-off effect in the infrared region. Conversely, the insulating HVO2 film maintained high transparency in both visible light and infrared regions. For example, the transmittance at 650 nm for the pristine VO2 film and metallic HxVO2 was about 56%, while that of the insulating HVO2 film was increased up to 72%. In the infrared region, the transmittance difference at 2000 nm for the pure VO2 film across the MIT process (25° and 90°C) was about 40.3%, while the change from the metallic HxVO2 film to the insulated HVO2 film reached 49.1%.

Fig. 5 Optical properties in relation to possible smart window applications.

(A) The schematic diagram of an electrochromic smart window. Properties of three films with different phases are compared. Both the pure VO2 film and the gating-produced metallic HxVO2 film show a similar yellowish color, while the HVO2 film is almost transparent. USTC, University of Science and Technology of China. (B) Optical transmittance spectra of VO2, HxVO2, and HVO2 thin films. The transmittance at 650 nm for the pristine VO2 film and metallic HxVO2 is about 56%, while the insulating HVO2 film has an increased transmittance of 72%. In the infrared region, the transmittance difference at 2000 nm for the pure VO2 film across the MIT process (transmittance of film at 25°C compared to 90°C) is about 40.3%, while the change in transmittance from the metallic HxVO2 film to the insulating HVO2 film is higher at 49.1%. (C) A plot of luminous transmittance Tlum versus solar modulation ability ΔTsol that highlights the results of this work () compared to previously reported data.

On the basis of these spectral measurements, the integrated luminous transmittances (380 to 780 nm) and solar transmittances (350 to 2500 nm) can be calculated by the following equations (18)Tlum=Φlum(λ)T(λ)dλ/Φlum(λ)dλ(3)Tsol=Φsol(λ)T(λ)dλ/Φsol(λ)dλ(4)where T(λ) is the transmittance function, Φlum is equal to the standard luminous efficiency function for photopic vision, and Φsol represents the solar irradiance spectrum for an air mass of 1.5. The solar modulation ability (ΔTsol) of the metallic HxVO2 and insulating HVO2 films can be calculated byΔTsol=Tsol,insulatingHVO2Tsol,metallicH1xVO2(5)

According to the above formula, the transparent, heavily insulating HVO2 film exhibits a high Tlum value of about 70.8%, while the transition between the metallic and insulating phases of the H-doped VO2 film is accompanied by a good ΔTsol value of 26.5% (Fig. 5C). The data from previous reports for traditional VO2 smart windows (see table S2) are also plotted. The performance of a smart window based on the transition between the metallic and insulating phases of an H-doped VO2 film appreciably surpasses previous records. Furthermore, it even surpasses the theoretical limitation of the ΔTsol of ~23% for a traditional VO2 smart window, which can only be achieved by texture surface design or complex multiyear film fabrication (43).

For architectural smart coatings, the excellent luminous transmittance in the visible range and high modulation efficiency in the NIR regions are both important and greatly desirable. There are two long-lasting issues hindering the practical application of VO2 in smart windows: low luminous transmittance (Tlum) and poor solar energy regulation ability (ΔTsol). For a traditional smart window constructed with the pure VO2 film, increasing the VO2 film thickness is necessary for better infrared switching performace, and as a result, the visible light transmittance will be greatly decreased. This problem is caused by the intrinsic band structures and optical properties of VO2, making it very difficult to be solved for the theromochromic VO2 smart window. In addition, its relatively high critical temperature (~68°C) is another big obstacle for practical applications (14, 16). Thus, in this work, the voltage-controlled phase transitions between the metallic HxVO2 and insulating HVO2 films not only overcome the temperature issue by operating at room temperature but also demonstrate high Tlum and large ΔTsol values in Fig. 5C, showing the unique advantages for practical smart window applications.

DISCUSSION

In this study, we have achieved a reversible tristate phase transformation in a VO2 epitaxial film by using solid electrolyte–assisted electric field control. These gating voltage–controlled phase transitions originate from the insertion/extraction of hydrogens into/from the VO2 lattice. By changing the voltage, we can reversibly modulate the phase transformations among the insulating monoclinic VO2, the metallic H1−xVO2 (0 < x < 1), and the insulating HVO2 phase structures. The transition between the metallic HxVO2 phase and the insulating HVO2 phase shows pronounced electrochromic effects at room temperature with greatly enhanced luminous transmittance in the visible range and the highest modulation efficiency in the NIR regions. This system overcomes the primary weaknesses of the traditional VO2 smart window. Our findings thus demonstrate a facile route using phase modulation by a solid electrolyte for creating realistic energy-saving devices in the future.

MATERIALS AND METHODS

Thin-film growth

High-quality VO2 (020) epitaxial films were grown on an Al2O3 (0001) crystal substrate by radio frequency (rf) plasma–assisted oxide molecular beam epitaxy equipment; more details on film preparation were reported elsewhere (44).

Solid electrolyte preparation

NaClO4 (Sigma-Aldrich) dissolved in a PEO [molecular weight (Mw) = 100,000; Sigma-Aldrich] matrix was used as the solid electrolyte. NaClO4 and PEO powders (0.3 and 1 g, respectively) were mixed with 15 ml of anhydrous methanol (Alfa Aesar). The mixture was then stirred overnight at 50°C until a gel-like solid electrolyte was formed (45). A 10 mm by 10 mm electrolyte-covered VO2 thin-film FET structure with three terminals was fabricated.

Characterizations

Electrical properties were conducted by Keithley 2400 sourcemeters at room temperature. For the gating test, the voltage sweep rates were set to 1.0 V/2500 s for the fast mode and 1.0 V/10,000 s for the slow mode. Raman spectra (JY LabRAM HR, Ar+ laser at 514.5 nm, 0.5 mW) were recorded for different samples at room temperature. The laser spot size was 1 μm by 2 μm, and five points were tested for each film sample, which showed consistent results. The XPS (Thermo ESCALAB 250; Al Kα, 1486.7 eV) was used to examine the chemical states of the VO2 film samples before and after gating treatment. To detect the hydrogen concentration in the gated VO2 film sample, SIMS measurements (Quad PHI 6600) were conducted.

XANES was conducted at the x-ray magnetic circular dichroism (XMCD) beamline (BL12B) at the National Synchrotron Radiation Laboratory (NSRL), Hefei. The NSRL is a second-generation accelerator with a 0.8-GeV storage ring, which is suitable for soft x-ray experiments. Total electron yield mode was applied to collect the sample drain current under a vacuum higher than 3.0 × 10−10 torr. The energy range is 100 to 1000 eV with an energy resolution (ΔE/E) of 1.0 × 10−3 at 1.0 keV, and the beam size is about 1.0 mm by 3.0 mm. High-resolution synchrotron XRD curves were characterized at the BL14B beamline of the Shanghai Synchrotron Radiation Facility (SSRF). The SSRF is a third-generation accelerator with a 3.5-GeV storage ring. The BL14B beamline shows an energy resolution (ΔE/E) of 1.5 × 10−4 at 10 keV and a beam size of 0.3 mm by 0.35 mm with a photon flux of up to 2 × 1012 phs/s at 10 keV. Considering the photon flux distribution and the resolution, the 0.124-nm x-ray was chosen for the experiment.

First-principles calculations

All calculations were based on DFT, using the Vienna ab initio Simulation Package code (46). Exchange and correlation terms were described using general gradient approximation (GGA) in the scheme of Perdew-Burke-Ernzerhof (47). Core electrons were described by pseudopotentials generated from the projector-augmented wave method (48), and valence electrons were expanded in a plane-wave basis set with an energy cutoff of 480 eV. The GGA + U method was used to optimize the structure; U and J were chosen to be 4 and 0.68 eV, respectively. The relaxation was carried out until all forces on the free ions converged to 0.01 eV/Å. The climbing image nudged elastic band (49) method was used to find the minimum energy paths and the transition states for diffusion of H into VO2 and H-doped VO2.

SUPPLEMENTARY MATERIALS

Supplementary material for this article is available at http://advances.sciencemag.org/cgi/content/full/5/3/eaav6815/DC1

Fig. S1. Temperature-dependent gating-induced phase transitions.

Fig. S2. XPS spectra for the pure and gated VO2 samples.

Fig. S3. SIMS test for the gated VO2 film samples.

Fig. S4. Fourier transform infrared test for the residual methanol in PEO electrolyte.

Fig. S5. Stability test for the H-doped VO2 films.

Fig. S6. Raman spectra for the films.

Fig. S7. Atomic structures of H4V4O8.

Table S1. Formation energies calculations.

Table S2. Comparison of the solar energy regulation ability (ΔTsol) and luminous transmittance (Tlum) values for various VO2-based smart-windows.

References (5058)

This is an open-access article distributed under the terms of the Creative Commons Attribution-NonCommercial license, which permits use, distribution, and reproduction in any medium, so long as the resultant use is not for commercial advantage and provided the original work is properly cited.

REFERENCES AND NOTES

Acknowledgments: Funding: This work was partially supported by the National Key Research and Development Program of China (2018YFA0208603, 2016YFA0401004), the National Natural Science Foundation of China (U1432249, 11404095, 11574279, and 11704362), the Fundamental Research Funds for the Central Universities, the Youth Innovation Promotion Association CAS, the Major/Innovative Program of Development Foundation of Hefei Center for Physical Science and Technology, and the China Postdoctoral Science Foundation (2017M622002). This work was partially carried out at the USTC Center for Micro- and Nanoscale Research and Fabrication. We also acknowledge support from the XMCD beamline (BL12B), the photoelectron spectroscopy beamline (BL10B) at the NSRL (Hefei), and the x-ray diffraction beamline (BL14B1) at the SSRF. Author contributions: J.J. and C.Z. conceived the study. S.C. and C.Z. designed the experiments and performed the initial tests. Z.W. and J.J. conducted the theoretical calculations. S.C., H.R., Y.C., W.Y., C.W., and B.L. conducted the sample characterizations and synchrotron-based measurements. S.C., J.J., and C.Z. wrote the manuscript. All authors discussed the results and commented on the manuscript. Competing interests: The authors declare that they have no competing interests. Data and materials availability: All data needed to evaluate the conclusions in the paper are present in the paper and/or the Supplementary Materials. Additional data related to this paper may be requested from the authors.
View Abstract

Navigate This Article