Abstract
The pyrochlore manganate In2Mn2O7 is a very promising ferromagnetic semiconductor material, which has a good application prospect in spin transport due to its very low electron effective mass, high Curie temperature, and structural stability. In this paper, In2Mn2O7 with pyrochlore structure was successfully prepared by high temperature and high pressure combined with the sol–gel method, and the in situ high-pressure X-ray diffraction experiment was carried out on it. The results showed that the structure of In2Mn2O7 was very stable in the pressure range of 0–29.0 GPa, and its bulk modulus was given. This lays a foundation for the application of In2Mn2O7 in extreme environments.
Introduction
In the past decades, there has been increasing interest in the pyrochlore oxide materials (general formula A2B2O7) for the studies in both basic science [1, 2] and engineering [3]. Due to the tetrahedral geometry of cations in pyrochlore, very rich quantum phenomena were discovered recently. For example, Ho2Ti2O7 and Dy2Ti2O7 are Ising pyrochlore materials with Ising anisotropy and effective antiferromagnetic exchange interaction [4]. They have classical spin-ice ground state, and the magnetic moment at each tetrahedral vertex forms a two-in and a two-out degenerate distribution. Besides, the anomalous Hall effect is found in Nd2Mo2O7 [5], the giant magnetoresistance in Ti2Mn2O7 [6], and the topological state in A2Ir2O7 [7].
Materials combining semiconductivity and magnetism open up possibilities for novel electronic devices that utilize electron spin in addition to charge degrees of freedom [8, 9]. The ferromagnetic semiconductor has attracted special attention because of its spin polarization transport potential in spintronics. A closely related important technical phenomenon is spin filtering, which can be achieved by using ferromagnetic semiconductors as tunneling barriers to generate high spin polarization currents [10, 11]. Ferromagnetic semiconductors used in spintronics are mainly based on magnetic impurities embedded in conventional non-magnetic semiconductors [12]. The robustness of carrier-induced ferromagnetism is very sensitive to the growth conditions and processing methods. The origin of room-temperature ferromagnetism of doped magnetic semiconductors is still a controversial topic. In contrast, undoped magnetic semiconductors exhibit long-range magnetism independent of external doping. At present, some undoped ferromagnetic semiconductors have been reported, mainly including halide CrBr3 [13], CrI3 [14–16], Mn-based pyrochlore oxide [17], perovskite oxide BiMnO3 [18], CuSeO3 [19], and YTiO3 [20]. The ferromagnetic semiconductor most studied in spintronics is europium chalcogenide compound EuX (X = O, S, Se) [10, 21–24]. EuX has good performance in spin filter devices, but the Curie temperature is very low [e.g., Tc(EuO) = 69 K [25]], which is a characteristic of most ferromagnetic semiconductors currently known. In addition, the electronic structure of ferromagnetic semiconductors needs to be adjusted in the context of spin transport. The electron injection efficiency is determined by the exchange splitting of the conduction band, and low electron effective mass is the key to achieve high carrier mobility. Similarly, exchange splitting is also important for spin filtering because it produces spin-dependent tunneling current barriers.
Therefore, the combination of strong ferromagnetism and attractive semiconductor properties in a material is ideal, but it is still an issue that needs further study. Wei Chen et al. searched for undoped ferromagnetic semiconductors through high-throughput computational screening [26]. They found that magnetic pyrochlore oxide In2Mn2O7 has a good application prospect in spin transport due to its very low effective electron mass, large exchange splitting of conduction band, stability in air, and high Curie temperature of 130 K. Therefore, the study of the structural stability of In2Mn2O7 under high pressure is of great significance for the application of it under extreme conditions. In this paper, we have successfully synthesized pyrochlore In2Mn2O7. The structural stability In2Mn2O7 has been investigated by angle-dispersive synchrotron X-ray powder diffraction at high pressures.
Experiment
Sample Preparation
In this experiment, In2Mn2O7 was synthesized by the sol–gel method combined with the high-temperature and high-pressure (HTHP) method. In2O3 (99.99% purity), MnO (99.9% purity), citric acid (AR: analytical reagent), and nitric acid (AR) were used as raw materials. In2O3 and MnO with the molar ratio of 1:2 were dissolved in nitric acid and diluted in distilled water. Citric acid was then added as a fuel to the above solution to yield a citrate/nitrate ratio of 1.2. The mixed solution was continuously stirred using a magnetic agitator. The solution was evaporated by heating at 150°C until a brown sticky gel was formed. Subsequently, the gel was dried at a temperature up to 200°C. The dried gel was calcined at 500°C in air for 10 h.
Next, the target product was synthesized by the cubic anvil HPHT apparatus. The powder was pressed into cylindrical samples with a diameter of 6 mm and a height of 2.3 mm. The cylindrical sample was put into the sample synthesis chamber with a specific combination, and the chamber was put into the cubic anvil HPHT apparatus (SPD6×600) [27, 28]. The temperature was raised to 1,300°C, and the pressure was increased to 5 GPa. The heat and pressure preservation time was 60 min. At last, we made the temperature drop rapidly to room temperature within 15 s, and the pressure needed to be reduced slowly to obtain pyrochlore In2Mn2O7.
X-Ray Diffractometry
In the ambient condition, the phase purity was detected by powder X-ray diffraction (XRD) measurements using a Rigaku Rotaflex X-ray diffractometer with Cu-Kα radiation (λ = 1.54056Å) at room temperature. The test voltage was 40 kV, the current was 30 mA, the scanning range was 10–90°, and the scanning speed was 4°/min. The high-pressure angle-dispersive XRD patterns were collected at the beamline X17C of the National Synchrotron Light Source at Brookhaven for In2Mn2O7 with a monochromic wavelength of 0.4112 Å. A diamond anvil cell (DAC) with an anvil culet of 300 μm diameter was utilized to generate high pressure with the T301 stainless steel as the gasket, which was pre-indented to a 50 µm thickness. One piece of the as-prepared samples, a small piece of ruby as the pressure calibrant [29], and a 16:3:1 methanol/ethanol/water mixture as the pressure-transmitting medium were loaded into the diamond anvil cells. The distance between the sample and the detector and parameters of the detector were calibrated using a CeO2 standard. All the diffraction data were collected using an MAR CCD detector, and the diffraction profiles were obtained via the radial integration of the two-dimensional diffraction rings using FIT2D software [30]. Rietveld analyses were performed with the software GSAS [31].
Results and Analysis
XRD Analysis
The structure of In2Mn2O7 was determined by Rietveld refinement, shown in Figure 1A. The red, blue, and black lines in the figure represent the experiment curve, the calculation curve, and the difference between them, respectively. The green vertical line represents the fitted peak position. From the fitted results, it was determined that the compound In2Mn2O7 crystallized in the cubic system, with the space group Fd-3m (No. 227) and cell parameters a = 9.7113(5)Å, V = 915.8(6)Å3, and Z = 8. In2Mn2O7 can be formulated as In2Mn2O6O′, with Mn ions at 16c, In ions at 16d, O at 48f, and O′ at 8b. In ions formed twisted cubes with surrounding oxygen atoms, and Mn ions formed twisted octahedrons with surrounding oxygen atoms. It was worth noting that there was only one adjustable position parameter in this structure, which was the x coordinate of the oxygen atom at the position of 48f. Figure 1B is the schematic diagram of its structure. The refinement parameters of the cubic phase In2Mn2O7 structure are given in Table 1.
FIGURE 1
(A) Rietveld full-profile refinement of the diffraction patterns of In2Mn2O7 at ambient condition. Red, blue, and black solid lines represent experimental, calculated, and residual patterns, respectively. Vertical markers show the calculated peak positions. (B) A schematic representation of the crystal structures of pyrochlore-type In2Mn2O7.
TABLE 1
| Atoms | Wyckoff (x y z) |
|---|---|
| In | 16d (0.5 0.5 0.5) |
| Mn | 16c (0 0 0) |
| O(1) | 48f [0.125 0.125 0. 0.3241(9)] |
| O(2) | 8b (0.325 0.325 0.325) |
| Residuals1 (%) | Rwp: 6.27% |
| Rp: 5.08% | |
| Pressure (GPa) | Lattice parameter (Å) |
| 0.6 | 9.6983(7) |
| 1.6 | 9.6786(4) |
| 3.2 | 9.6474(3) |
| 5.0 | 9.6296(2) |
| 6.2 | 9.6087(7) |
| 7.4 | 9.5892(2) |
| 9.5 | 9.5707(1) |
| 10.8 | 9.5579(2) |
| 12.4 | 9.5390(3) |
| 14.0 | 9.5268(6) |
| 15.5 | 9.5102(1) |
| 17.3 | 9.4937(2) |
| 19.4 | 9.4788(4) |
| 21.0 | 9.4517(5) |
| 22.9 | 9.4368(5) |
| 27.0 | 9.3993(3) |
| 29.0 | 9.3764(2) |
Refined atomic coordinates of In2Mn2O7 at ambient condition and lattice parameters at various pressures.
Note: 1Rwp and Rp as defined in GSAS [29].
In Situ High-Pressure X-Ray Diffraction
The in situ XRD patterns of In2Mn2O7 at various pressures up to 29.0 GPa have been collected, and a few representative patterns are shown in Figure 2. The results showed that, in the whole pressure range of this experiment, there was no obvious change in the high-pressure XRD diffraction pattern, and there appeared no new diffraction peak. The diffraction peak under each pressure point moved to a higher angle with increasing pressures, accompanied by the weakening of the intensity of diffraction peak, which was usually caused by the increase of lattice disorder under pressure. This indicated that the cell volume of In2Mn2O7 decreased gradually in the test pressure range of 0–29.0 GPa. After releasing the pressure, the positions of diffraction peaks were almost the same as those before pressure rise. The above two points indicated that the cubic phase In2Mn2O7 exhibited excellent structural stability in the whole pressure range in this experiment. When the pressure increased gradually, the compound had no structural phase transition but only slightly strained, and this change disappeared completely after the pressure was removed. In order to further study the change of the crystal structure of In2Mn2O7 with pressure, Rietveld analyses were performed with the software GSAS under various pressures. We obtained the lattice constants given in Table 1 and volumes under different pressures as shown in Figure 3.
FIGURE 2
Angle-dispersive XRD patterns of In2Mn2O7 at selected pressures with a monochromic wavelength of 0.4112 Å at room temperature. The top red pattern was taken from the samples after the release of pressure.
FIGURE 3
Observed P–V variation fitted with the third-order Birch–Murnaghan (B–M) equation of state for In2Mn2O7. Birch–Murnaghan EOS fits for the data are shown with the dotted line, B = 221(6) GPa, B′o = 5.5(1.2), and solid line, B = 240(4) GPa, B′o held at 4. The inset shows the pressure dependence of the x parameter for the O48f atom.
The P–V data were fitted using the Birch–Murnaghan (B–M) equation of state [32], expressed as follows:where B0 represents the bulk modulus at zero pressure, B′o represents the first derivative of the bulk modulus, and V0 represents the volume of a single cell at zero pressure. Taking B′o= 4, the fitting results are shown as the red curve in Figure 3. It can be seen that the red curve fitted very well with the experimental data within the experimental pressure range, and the fitting results showed that B0 = 240(4) GPa. In addition, when B′o was not fixed as 4, we obtained B = 221(6) GPa and B′o = 5.5(1.2), shown with the fluorescent green dotted line in Figure 3. This result was compared with the bulk moduli of other A2B2O7 pyrochlore oxides. The bulk moduli of A2Ti2O7 (A = Ho, Y, Tb, Sm) compounds were 213(2), 204(3), 199(1), and 164.8(1.5) GPa [33, 34], and the bulk moduli of A2Sn2O7 (A = La, Eu) compounds were 180(6) and 170 GPa, respectively [35]. It can be seen that the bulk modulus of In2Mn2O7 was obviously larger than that of the above compounds. However, we also studied A2Ge2O7 (A = In, Ho, Sc) oxides before and obtained that their bulk moduli were 279(4), 328(7), and 263(4) GPa, respectively [36–38]. The bulk modulus is one of the most important physical parameters that characterize the mechanical property of materials. Several works have suggested that the bond length should be taken into account to explain the variation of the bulk modulus of materials [39, 40]. It has been known that the bulk modulus is proportional to k/dn, where d is the bond length and k, n are determined by the properties of materials [40, 41]. Changes in the electronic configuration of the A and B atoms of A2B2O7 pyrochlore oxides have an effect on the length of the bond. Ionic, covalent, and metallic bonds can affect bond strength which is closely related to the bond length. So to find the laws and the physical mechanisms behind these bulk moduli, further research is needed.
In the ordered cubic pyrochlore structure, all the atoms are in special positions except O48f. Hence, the structure is entirely described by the x positional parameter of O48f. The X-ray diffraction patterns were refined by the Rietveld method up to 29.0 GPa. The refined x parameter for O48f as a function of pressure is shown in the inset of Figure 3. Previous studies on pyrochlore oxides have revealed that the sudden change of the x positional parameter of the O48f atom existed in the process of pressure-induced structural phase transition. For example, with increasing pressure, the ordered pyrochlore Gd2Zr2O7 begins to transform to a disordered defect-fluorite–type cubic structure up to 15 GPa. Above 15 GPa, a high-pressure phase forms that has a distorted defect-fluorite–type structure of lower symmetry. Below 10 GPa, there is no or little change in the refined x parameter for O48f, followed by a rapid decrease with increasing pressure [42]. Above 18 GPa, the pyrochlore Sm2Zr2O7 is unstable, and a pressure-induced phase transition occurred. The x coordinate for the 48f oxygen increases dramatically after 16 GPa [43]. Within the range of our study, it can be seen that xO48f has no sudden change, which also indicates the structural stability of pyrochlore In2Mn2O7.
Conclusion
In this paper, the manganate In2Mn2O7 was successfully prepared by the sol–gel method combined with high temperature and high pressure. Through XRD characterization at atmospheric pressure, In2Mn2O7 was identified as a pyrochlore structure, and its exact crystallographic data and structural refinement parameters were given. Through in situ high-pressure X-ray diffraction, it was found that In2Mn2O7 had no structural phase transition below 29.0 GPa, showing excellent structural stability. By fitting the P–V curve with the Birch–Murnaghan (B–M) equation of state, the bulk modulus of the sample was obtained as 240(4) GPa. This lays a foundation for the application of In2Mn2O7 in extreme environments.
Statements
Data availability statement
The original contributions presented in the study are included in the article/supplementary material, and further inquiries can be directed to the corresponding authors.
Author contributions
XW contributed to the conception and design of the study and completed the high-pressure part of the experiment. HL completed sample synthesis. HL and SM performed the design of figures and wrote the first draft of the manuscript. JY organized the literature. All authors contributed to manuscript revision and read and approved the submitted version.
Funding
This research was supported by the Guangxi Natural Science Foundation under Grant Nos. 2018GXNSFBA050034 and 2019GXNSFBA185001, the Open Project of State Key Laboratory of Superhard Materials (Jilin University) (202107), and the Young and Middle-aged Teachers’ Basic Ability Improvement Project of Guangxi Department of Education (No. 2020KY04023).
Acknowledgments
We acknowledge Zhiqiang Chen and Xinguo Hong for technical support with the high-pressure experiments at the X17C beamline of the NSLS.
Conflict of interest
The authors declare that the research was conducted in the absence of any commercial or financial relationships that could be construed as a potential conflict of interest.
Publisher’s note
All claims expressed in this article are solely those of the authors and do not necessarily represent those of their affiliated organizations, or those of the publisher, the editors, and the reviewers. Any product that may be evaluated in this article, or claim that may be made by its manufacturer, is not guaranteed or endorsed by the publisher.
References
1.
GardnerJSGingrasMGreedanJE. Magnetic Pyrochlore Oxides[J]. Rev Mod Phys (2010) 82(1). 10.1103/revmodphys.82.53
2.
HassanAKLévyLPDarieCStrobelP. Macroscopic Anisotropy and Symmetry Breaking in the Pyrochlore antiferromagnetGd2Ti2O7. Phys Rev B (2003) 67(21):214432. 10.1103/physrevb.67.214432
3.
LutiqueSStaicuDKoningsRJMRondinellaVVSomersJWissT. Zirconate Pyrochlore as a Transmutation Target: thermal Behaviour and Radiation Resistance against Fission Fragment Impact. J Nucl Mater (2003) 319(none):59–64. 10.1016/s0022-3115(03)00134-x
4.
TomaselloBCastelnovoCMoessnerRQuintanillaJ. Single-ion Anisotropy and Magnetic Field Response in the Spin-Ice Materials Ho2Ti2O7 and Dy2Ti2O7. Phys Rev B (2015) 92:155120. 10.1103/PhysRevB.92.155120
5.
KatsufujiTHwangHYCheongS-W. Anomalous Magnetotransport Properties ofR2Mo2O7near the Magnetic Phase Boundary. Phys Rev Lett (2000) 84(9):1998–2001. 10.1103/physrevlett.84.1998
6.
ShimakawaYKuboYManakoT. Giant Magnetoresistance in Ti2Mn2O7 with the Pyrochlore Structure. Nature (1996) 379(6560):53–5. 10.1038/379053a0
7.
WanXTurnerAMVishwanathASavrasovSYTopological Semimetal and Fermi-Arc Surface States in the Electronic Structure of Pyrochlore Iridates[J]. Phys Rev (2011) 83(20):205101.1–205101.9. 10.1103/physrevb.83.205101
8.
PrinzGA. Magnetoelectronics. Science (1998) 282(5394):1660–3. 10.1126/science.282.5394.1660
9.
ZuticIFabianJSarmaSD. Spintronics: Fundamentals and Applications[J]. Rev Mod Phys (2004) 76(2):323–410. 10.1103/RevModphys.76.323
10.
EsakiLStilesPJMolnarSv.Magnetointernal Field Emission in Junctions of Magnetic Insulators. Phys Rev Lett (1967) 19(15):852–4. 10.1103/physrevlett.19.852
11.
MooderaJSHaoXGibsonGAMeserveyR. Electron-Spin Polarization in Tunnel Junctions in Zero Applied Field with Ferromagnetic EuS Barriers. Phys Rev Lett (1988) 61(5):637–40. 10.1103/physrevlett.61.637
12.
SatoKBergqvistLKudrnovskyJDederichsPHErikssonOTurekIet alFirst-principles Theory of Dilute Magnetic Semiconductors[J]. Rev Mod Phys (2014) 82(2):1633–90.
13.
TsubokawaI. On the Magnetic Properties of a CrBr3 Single Crystal. J Phys Soc Jpn (1960) 15(9):1664–8. 10.1143/jpsj.15.1664
14.
DillonJFOlsonCE. Magnetization, Resonance, and Optical Properties of the Ferromagnet CrI3. J Appl Phys (1965) 36(3):1259–60. 10.1063/1.1714194
15.
McguireMADixitHCooperVRSalesBC. ChemInform Abstract: Coupling of Crystal Structure and Magnetism in the Layered, Ferromagnetic Insulator CrI3[J]. Cheminform (2015) 46(11):612–20. 10.1002/chin.201513017
16.
HuangBClarkGNavarro-MoratallaEKleinDRChengRSeylerKLet alLayer-dependent ferromagnetism in a van der Waals crystal down to the monolayer limit. Nature (2017) 546(Jun.8):270–3. 10.1038/nature22391
17.
GardnerJSGingrasMJPGreedanJE. Magnetic Pyrochlore Oxides. Rev Mod Phys (2010) 82(1):53–107. 10.1103/revmodphys.82.53
18.
GajekMBibesMBarthélémyABouzehouaneKFusilSVarelaMet alSpin Filtering through Ferromagnetic BiMnO[J]. Phys Rev B, Condensed matter (2005) 72(2):020406. 10.1103/physrevb.72.020406
19.
KohnKAkimotoS-i.InoueKAsaiKHorieO. Crystal Structure and Magnetic Properties of MnSeO3, CoSeO3, NiSeO3 and CuSeO3. J Phys Soc Jpn (1975) 38(2):587. 10.1143/jpsj.38.587
20.
GarrettJDGreedanJEMacleanDA. Crystal Growth and Magnetic Anisotropy of YTiO3. Mater Res Bull (1981) 16(2):145–8. 10.1016/0025-5408(81)90074-x
21.
MooderaJSMeserveyRHaoX. Variation of the Electron-Spin Polarization in EuSe Tunnel Junctions from Zero to Near 100% in a Magnetic Field. Phys Rev Lett (1993) 70(6):853–6. 10.1103/PhysRevLett.70.853
22.
SantosTSMooderaJS. Observation of Spin Filtering with a Ferromagnetic EuO Tunnel Barrier[J]. Phys Rev B (2004) 69(69):1681–5. 10.1103/physrevb.69.241203
23.
SantosTSMooderaJSRamanKVNegusseEHolroydJDvorakJet alDetermining Exchange Splitting in a Magnetic Semiconductor by Spin-Filter Tunneling. Phys Rev Lett (2008) 101(14):147201. 10.1103/physrevlett.101.147201
24.
WachterP. Chapter 19 Europium Chalcogenides: EuO, EuS, EuSe and EuTe. Handbook Phys Chem Rare Earths (1979) 2:507–74. 10.1016/s0168-1273(79)02010-9
25.
McguireTRShaferMW. Ferromagnetic Europium Compounds. J Appl Phys (1964) 35(3):984–8. 10.1063/1.1713568
26.
ChenWGeorgeJVarleyJBRignaneseGMHautierG. High-throughput Computational Discovery of In2Mn2O7 as a High Curie Temperature Ferromagnetic Semiconductor for Spintronics[J]. npj Comput Mater (2019) 5(1):1–7. 10.1038/s41524-019-0208-x
27.
ZhuPWJiaXChenHYGuoWLChenLXLiDMet alA New Method of Synthesis for Thermoelectric Materials: HPHT[J]. Solid State Commun (2002) 123(1-2):43–7. 10.1016/s0038-1098(02)00182-5
28.
MaSBaoKTaoQHuangXZhuPCuiT. An Ultra-incompressible Ternary Transition Metal Carbide. RSC Adv (2014) 4(108):63544–8. 10.1039/c4ra13193b
29.
MaoHKBellPM. Carnegie Institution of Washington Year Book, 77. Washington: Carnegie Institute (1978). p. 904.
30.
HammersleyAPSvenssonSOHanflandMFitchANHausermannDTwo-dimensional Detector Software: From Real Detector to Idealised Image or Two-Theta Scan[J]. High Press Res (1996) 14(4-6):14. 10.1080/08957959608201408
31.
LarsonACDreeleR. Generalized Structure Analysis System. Washington, D.C.: GSAS (2000).
32.
BirchF. Finite Strain Isotherm and Velocities for Single-crystal and Polycrystalline NaCl at High Pressures and 300°K. J Geophys Res (1978) 83:1257–68. 10.1029/jb083ib03p01257
33.
ScottPRMidgleyAMusaevOMuthuDVSSinghSSuryanarayananRet alHigh-pressure Synchrotron X-ray Diffraction Study of the Pyrochlores: Ho2Ti2O7, Y2Ti2O7and Tb2Ti2O7. High Press Res (2011) 31(1):219–27. 10.1080/08957959.2010.548333
34.
ZhangFManounBSaxenaSZhaCS. Structure Change of Pyrochlore Sm2Ti2O7 at High Pressures[J]. Appl Phys Lett (2005) 86(18):1906. 10.1063/1.1925307
35.
ZhaoYLiNXuCLiYZhuHZhuPet alAbnormal Pressure‐Induced Photoluminescence Enhancement and Phase Decomposition in Pyrochlore La 2 Sn 2 O 7. Adv Mater (2017) 29(34):1701513. 10.1002/adma.201701513
36.
LiHLiYLiNZhaoYZhuHZhuPet alA Comparative Study of High Pressure Behaviors of Pyrochlore-type and Thortveitite-type In2Ge2O7[J]. RSC Adv (2015) 5.
37.
LiHLiNZhuPWangX. A Comparative Study of High-Pressure Behaviors of the Two Polymorphs of Ho2Ge2O7. RSC Adv (2020) 10(18):10540–5. 10.1039/c9ra10428c
38.
LiHMaSYuZZhuHLiN. In-situ High-Pressure X-ray Diffraction of the Two Polymorphs of Sc2Ge2O7[J]. AIP Adv (2020) 10(9). 10.1063/5.0021334
39.
ZhangSLiHLiLZhouS. Calculation of Bulk Modulus on Carbon Nitrides with Chemical Bond Method. Appl Phys Lett (2007) 91:251905. 10.1063/1.2826269
40.
GaoF. Hardness Estimation of Complex Oxide Materials. [J] Phys Rev B (2004) 69:094113. 10.1103/physrevb.69.094113
41.
LiuAYCohenML. Prediction of New Compressibility Solids. J Sci (1989) 245(4920):841–2. 10.1126/science.245.4920.841
42.
ZhangFXLianJBeckerUEwingRCHuJSaxenaSK. High-pressure Structural Changes in theGd2Zr2O7pyrochlore. Phys Rev B (2007) 76(21):214104. 10.1103/physrevb.76.214104
43.
ZhangFLianJBeckerUWangLMHuJZSaxenaSet alStructural Distortions and Phase Transformations in Sm2Zr2O7 Pyrochlore at High Pressures [J]. Chem Phys Lett (2007) 441(4):216–20. 10.1016/j.cplett.2007.05.018
Summary
Keywords
pyrochlore, manganate, high pressure, high temperature, structural stability
Citation
Li H, Ma S, Ye J and Wang X (2021) Structural Stability of Pyrochlore Manganate In2Mn2O7 Under High Pressure. Front. Phys. 9:783136. doi: 10.3389/fphy.2021.783136
Received
25 September 2021
Accepted
17 November 2021
Published
15 December 2021
Volume
9 - 2021
Edited by
Ralph Ernstorfer, Technical University of Berlin, Germany
Reviewed by
Surajit Chatterjee, University of Michigan, United States
Hiroshi Fukui, Japan Synchrotron Radiation Research Institute, Japan
Updates
Copyright
© 2021 Li, Ma, Ye and Wang.
This is an open-access article distributed under the terms of the Creative Commons Attribution License (CC BY). The use, distribution or reproduction in other forums is permitted, provided the original author(s) and the copyright owner(s) are credited and that the original publication in this journal is cited, in accordance with accepted academic practice. No use, distribution or reproduction is permitted which does not comply with these terms.
*Correspondence: Shuailing Ma, msljlu@163.com; Xin Wang, xin_wang@jlu.edu.cn
This article was submitted to Physical Chemistry and Chemical Physics, a section of the journal Frontiers in Physics
Disclaimer
All claims expressed in this article are solely those of the authors and do not necessarily represent those of their affiliated organizations, or those of the publisher, the editors and the reviewers. Any product that may be evaluated in this article or claim that may be made by its manufacturer is not guaranteed or endorsed by the publisher.