The chemical reaction of inert xenon (Xe), a quintessential full-shell element, was earliest predicted by Pauling in 1933 and the first xenon compound was experimentally produced in 19621. Then, more xenon compounds were experimentally synthesized at ambient pressure, containing some most electronegative atoms like fluorine2,3,4,5 or oxygen6,7,8,9. Subsequently, scientists found that pressure can effectively improve the chemical reactivity of Xe10,11,12,13,14,15,16,17. At moderate pressures, solid xenon forms weakly bonded compounds with other species, e.g., with H2O10 and O211,12 at 1 and 3 GPa, respectively. Strikingly, several novel Xe compounds with unusual stoichiometries are found to be thermodynamically stable at high pressures, e.g., Xe oxides13,14, Xe nitrides15, xenon-hydrogen16, and Xe–Mg compounds17.

At ultra-high-pressure conditions, the high volatility, relative chemical inertia, and abundant isotopes of xenon make it a valuable tracer in the study of evolutionary dynamics and history of Earth. However, 99% of Earth’s primordial Xe is mysteriously missing as characterized by its very low abundance compared to other noble gases in Earth’s atmosphere18, which is known as the missing Xe problem19. Early hypotheses proposed that Xe might have escaped from the atmosphere after ionization20,21,22, or that it might be stored in the interior of Earth23,24,25,26,27,28,29. Attempts to incorporate Xe into ices, clathrates and sediments in the Earth’s crust were not successful27,28,29. Laboratory experiments have succeeded in trapping Xe in quartz30,31 and observing predicted stable xenon oxides13,14,32; but these results cannot explain the missing Xe mystery, because xenon oxides are unstable in equilibrium with metallic iron in lower mantle while xenon silicates decompose spontaneously at mantle pressures13. Reactions of Xe with iron and nickel in Earth’s core were predicted as a viable scenario33 and the predicted compounds were synthesized under core pressure and temperature conditions32,34. However, it remains highly intriguing and challenging to explore possible capture and stabilization of Xe by suitable minerals in Earth’s mantle, which is of special significance because it was estimated that the loss of atmospheric Xe occurred about 100 million years from accretion, corresponding to the time of mantle differentiation event30.

Extensive past searches were unable to find chemical reactions of Xe with known mantle minerals. Recently discovered FeO2 synthesized at lower mantle conditions35 and stablized above 74 GPa in theoretical calculation36, offer an intriguing new possibility. This newly identified iron peroxide is able to react with helium to form a rare helium-bearing compound that explains deep-Earth primordial helium deposits revealed by geochemical evidences37. This finding raises exciting prospects that FeO2 may be able to react with Xe (actually PT stability range of FeO2 has not been completely established in experiments) at mantle conditions, thereby forming compounds capable of trapping Xe in Earth’s interior. In this work, we have explored possible reactions of Xe with FeO2 in contrast with known mantle constituents FeO, SiO2, MgO, CaO, and Al2O3. We find that FeO2 has unique ability to react with Xe and form robust Xe-Fe oxides Xe2FeO2 and XeFe3O6 with surprisingly strong Xe–O bonding, while other mantle oxides do not react with Xe. We have further examined mass density and sound velocities of these Xe-Fe oxides, and the results support their viability in vast lower mantle region. These findings establish robust materials basis, formation mechanism, and geological viability of these Xe-Fe oxides, which advance fundamental knowledge for understanding xenon chemistry and physics mechanisms for the possible deep-Earth Xe reservoir.


Crystal structures

We take the crystal phases identified by the structure search process at various FeO2: Xe ratios and compute their enthalpy to determine the most viable structure at each composition, and based on the obtained results we construct the convex hull, as shown in Fig. 1a, which indicates stable products from reactions of FeO2 and Xe. This exercise has led to the discovery of two Xe-Fe oxides, Xe2FeO2 and XeFe3O6, that are stable against decomposition at 150 GPa and 200 GPa. The pressure–volume terms, associated with packing efficiency, make the major contribution to guarantee the thermodynamical stability of Xe2FeO2 and XeFe3O6 with formation enthalpies lying on the convex hull (Supplementary Fig. 1). These two Xe-Fe oxides are both still stable relative to all possible binary phases or pure simple substances of Xe-Fe-O2, which can be seen in Supplementary Information (Supplementary Figs. 2 and 3). The details Phonon dispersions calculated at 150 GPa (Fig. 1b, c) show that these compounds are dynamically stable and, as will be shown below, thermal effects further stabilize both oxides over a wider range of pressure at elevated temperatures at deep-Earth conditions. Here we first present a full analysis of structural and bonding characters of these two oxides at 150 GPa as a representative case study. The compound Xe2FeO2 is crystalized in a monoclinic structure with P21/c symmetry (Fig. 1d); its structural motif consists of stacked layers of corner-sharing octahedron with each Fe atom surrounded by six O atoms and the Fe atom is centered in a slightly distorted octahedron containing Fe–O bond lengths in a narrow range of 1.79–1.82 Å at 150 GPa. Each Xe atom in this structure has a coordination number of 3, bonding at the corners of FeO6 octahedra with the Xe–O bond lengths in the range of 2.40–2.42 Å at 150 GPa, which are similar to those found in Xe2O3 (~2.50 Å) and Xe2O5 (~2.37 Å) at the same pressure38. Meanwhile, XeFe3O6 is stabilized in a triclinic structure with P-1 symmetry, containing two formula units per cell (Fig. 1e); its corner-sharing FeO6 octahedra host Fe–O bonds with lengths of 1.73–1.81 Å at 150 GPa, forming a tubular structure, and each Xe atom has a coordination number of 6, located in the Fe-O tube with the nearest Xe-O distance of 2.08 Å, resulting in the vibrational mode of the lowest-frequency branch at F as shown in Fig. 1c. Further vibrational analyses are shown in Supplementary Fig. 4 and structural details of both Xe-Fe oxides at 150 GPa are listed in Supplementary Information (Supplementary Table 1).

Fig. 1: Energetic stability and structures of Xe-Fe oxides.
figure 1

a The ground-state convex hull with solid lines for the FeO2-Xe system constructed from calculated formation enthalpy (ΔH) data, identifying two stable Xe-Fe oxides, Xe2FeO2 and XeFe3O6, at 150 GPa and 200 GPa. The solid and open symbols represent the stable structures lying on the convex hull and the unstable structures above the convex hull, respectively. b Phonon dispersions of Xe2FeO2 at 150 GPa. c Phonon dispersions of Xe3FeO6 at 150 GPa. d The structure of Xe2FeO2 with a polyhedral and an enlarged view. e The structure of Xe3FeO6 with a polyhedral and an enlarged view. Xe, Fe, and O atoms are, respectively, shown in purple, gray, and red spheres.


Chemical Bonding

To assess bonding characters in the two Xe-Fe oxides, we have calculated their electronic density of states (DOS) at 150 GPa. The results shown in Fig. 2a, c reveal metallic nature of these compounds; crucially, in both cases the DOS in the vicinity of the Fermi level contain significant contributions from the Fe 3d, Xe 5p and O 2p states, indicating considerable Fe–O and Xe–O bonding interactions. We further calculated projected crystal orbital Hamiltonian population (pCOHP) that evaluates weighted population of wavefunctions on two atomic orbitals of a pair of selected atoms39. The results in Fig. 2b, d reveal characteristic Fe–O and Xe–O covalent bonding as indicated by the prominent features of strong low-energy bonding states together with some occupied antibonding states near the Fermi level in each case. It is noted that the occupied bonding states in Xe2FeO2 occur deeper below the Fermi level compared to those in XeFe3O6, indicating higher stability of Xe2FeO2. Moreover, integrated COHP (ICOHP) provides an estimate of the overall bonding strength39. Calculated ICOHP values for the Fe–O and Xe–O bonds at 150 GPa are -1.45 eV/pair and −0.24 eV/pair in XeFe3O6 and −1.01 eV/pair and −0.12 eV/pair in Xe2FeO2, respectively. These results show considerable Xe–O bonding compared to the strong Fe–O bonding, in sharp contrast to recently discovered He-FeO2 compound where He atoms show little direct bonding37 but instead serve as a Coulomb shield in stabilizing the structure40. We also examined charge distribution in Xe2FeO2 and XeFe3O6 by a Bader charge analysis41, and the results reveal a considerable amount of highly unusual charge transfer from Fe and Xe to O atoms. At 150 GPa, the Bader partial charges in Xe2FeO2 are +0.30, +1.40, −1.00 for Xe, Fe, and O, respectively; meanwhile, Bader partial charges in XeFe3O6 are +1.35, +1.35, −0.90 for Xe, Fe, and O, respectively, at the same pressure. As a result, Xe atoms in XeFe3O6 can donate more electrons than in Xe2FeO2 and Xe atoms can display different valence states in FeO2–Xe compounds. These significant charge transfers once again indicate strong bonding formation involving Xe, which is rare among noble gases atoms.

Fig. 2: Electronic properties of the two Xe-Fe oxides at 150 GPa.
figure 2

a Projected density of states (PDOS) of Fe-d, O-p, and Xe-p orbitals in Xe2FeO2. b Projected crystal orbital Hamiltonian Population (-pCOHP) of the newly predicted Xe2FeO2 compound. The values of -pCOHP >0 signify bonding states and the values of -pCOHP <0 signify antibonding states. c PDOS of Fe-d, O-p, and Xe-p orbitals in XeFe3O6. d -pCOHP of the newly predicted XeFe3O6 compound. The Fermi energy is set to zero of the energy.

Thermal effect

Thermal effects play a crucial role in material stability at pertinent geophysical conditions, where temperatures reach 2000–4500 K. Here, we evaluate Gibbs free energy of Xe2FeO2 and XeFe3O6 by calculating lattice contributions to the entropic term using the quasiharmonic approximation to account for volume dependence of phonon frequencies due to temperature induced lattice expansion. In Fig. 3a we present relevant energetic terms affecting structure stability. It is seen that internal energy U values of the two Xe-Fe oxides are higher than those of their separate constituents, namely Xe and FeO2, but the PV terms are decisively favorable and dominant, producing the lower enthalpy H for the formation of both oxides. The temperature effect (i.e., thermal vibration of atomic positions) are favorable to reduce Gibbs free energy G of the Xe-Fe oxides even more relative to their separate constituents, further stabilizing the resulting crystal structures. Consequently, the threshold pressure above which these oxides are stable reduces considerably at increasing temperatures, thereby significantly expanding their stability field as will be seen in the phase diagram presented below.

Fig. 3: Calculated energetic terms and the mean square deviations.
figure 3

a Various energetic term (ΔE) for the two Xe-Fe oxides, enthalpy (H), pressure–volume (PV) terms, internal energy (U), and Gibbs free energy (G) at 150 GPa, 2000 K. b Mean square deviations (MSD) of Xe, O, and Fe atomic positions in Xe2FeO2 at 150 GPa, 3000 K. c MSD of Xe, O, and Fe atomic positions in XeFe3O6 at 150 GPa, 3000 K.

Phase diagram

For a full assessment of temperature effects, we have performed extensive energetic and ab initio molecular dynamics (AIMD) simulations to evaluate structural stability and construct pressure–temperature (PT) phase diagram for the Xe-Fe oxide system. We present in Fig. 3b, c the mean square deviations (MSD) of atomic positions in the Xe-Fe oxides at typical high PT conditions of 150 GPa and 3000 K, and the results show that the Fe, O, and Xe atoms all remain near their lattice sites, indicating stability of the crystal structure. Similar AIMD simulations were performed systematically to probe each phase and determine the boundary where temperature-driven instability sets as indicated by deviating MSD from equilibrium positions; meanwhile Gibbs free energies were computed and compared to determine the boundaries between different solid phases in the PT space. The resulting phase diagram (Fig. 4) spans a wide PT range covering the lower mantle and higher PT regions.

Fig. 4: The Pressure–temperature (PT) phase diagram of the Xe-FeO2 system.
figure 4

The dotted and dashed lines indicate phase boundaries and temperature-driven phase instability, which are determined by Gibbs free energy and ab initio molecular dynamics (AIMD) calculations, respectively. The square symbols show phase transition points based on relative Gibbs free energy, and the solid and open triangle symbols represent stable and temperature-driven unstable solid phases, respectively, determined by AIMD simulations. The PT regions of stable Xe2FeO2 are covered by slash lines and the PT regions of stable XeFe3O6 are filled by back-slash. The pressure boundary between the lower mantle and the core is shown at the top of the figure. Also shown is the geotherm of the Earth’s interior65.

We now analyze the stability fields of the predicted Xe-Fe oxides under the (P, T) conditions conforming to geological constraints dictated by the geotherm that is also shown in Fig. 4. It is seen that Xe2FeO2 is stable in the pressure range 110-120 GPa and temperatures around 2500 K inside the geotherm corresponding to the deep lower mantle region; meanwhile, both Xe2FeO2 and XeFe3O6 are stable between pressures 120–136 GPa and temperatures 2500–3600 K inside the geotherm corresponding to the lowest mantle to core-mantle boundary (CMB); finally, as pressure and temperature rise further, Xe2FeO2 becomes the sole stable phase.

The above results suggest stable Xe-Fe oxides under the (P, T) conditions in vast deep-Earth regions. It is, however, necessary to assess the viability of the predicted Xe-Fe oxides in geological environments by examining their key material characteristics. To this end, we have run AIMD simulations to determine crystal structures at selected (P, T) conditions and used an AIMD-based strain-stress method42,43 to calculate the elastic tensors, from which elastic-wave velocities were determined by solving the Christoffel equation det |Tik-δikρV2 | = 0, where δik is the Kronecker delta function, V is one of the seismic velocities, and Tik is the Christoffel stiffness44.

Mass density and sound velocities

We examine mass density and mean compressional (P-wave) and shear (S-wave) sound velocities, VP and VS, respectively, at two representative (P, T) points: (120 GPa, 2500 K) for lower mantle, and (135 GPa, 3500 K) for CMB, and compare with geological data. We first examine XeFe3O6, whose stability field compared to the geotherm indicates its stability in the lower mantle and CMB regions, but higher temperatures destabilize this compound. The calculated densities of XeFe3O6 are 8.86 and 9.06 g/cm3 at the selected lower mantle and CMB (P, T) points, respectively, which lie within or close to the range of 4.95–9.90 g/cm3 from the core rigidity zone (CRZ) model and the range of 5.57–8.91 g/cm3 from the ultralow velocity zone (ULVZ) model45. The calculated VP (VS) are 8.94(4.03) km/s and 9.20(4.26) km/s, respectively, which lie within the range of 8.20–10.70 km/s (1.00–5.00 km/s) for the ULVZs45. All these results indicate that XeFe3O6 is a viable constituent at the lower mantle and CMB (P, T) conditions.

The calculated densities of Xe2FeO2 are 9.78 and 9.87 g/cm3 at the lower mantle and CMB points, respectively, which lie outside the range of 5.57–8.91 g/cm3 from the ULVZ model and at the top of the range of 4.95–9.90 g/cm3 from the CRZ model45. The calculated VP (VS) are 7.83(4.21) km/s and 7.94(4.02) km/s at the lower mantle and CMB points, respectively. While these VS values lie within the range of 1.00–5.00 km/s from the CRZ model or the range 2.91–6.17 km/s from the ULVZ model45, the VP values are out of the range of 10.97–13.03 km/s from the ULVZ model or the range of 8.20–10.70 km/s from the CRZ model45. These results render Xe2FeO2 a marginal lower mantle or CMB constituent at best.

Reaction of noble gases and deep-Earth constituents

Finally, we highlight several significant aspects on the special role of FeO2 in trapping Xe in deep Earth. First, we have systematically examined possible reaction of Xe with major deep-Earth constituents FeO, SiO2, MgO, CaO, and Al2O3, and the resulting convex-hull data (Supplementary Fig. 5) show highly unfavorable energetics in all the cases, offering an underlying cause for unsuccessful past attempts to find Xe-bearing minerals in Earth’s mantle. Second, we have examined possible reactions of other noble gases Ne, Ar, and Kr with FeO2, and the results (Supplementary Fig. 6) indicate no tendency toward forming any stable noble-gas-Fe oxides up to 200 GPa. These results provide the possibility that Xe could be the sole inert element for reacting with deep-Earth constituents under mantle conditions. Moreover, while He-bearing compound FeO2He is found stable at CMB conditions, there is little direct bonding between He and Fe or O atoms in the compound37. Compared to Kr, Ar, Ne, and He, Xe has the lowest ionization energy and electronegativity, and consequently Xe is the easiest noble-gas atom to open up its outermost closed shell and form direct bonding as found in Xe2FeO2 and XeFe3O6.

In summary, we have identified two Xe-Fe oxides, Xe2FeO2 and XeFe3O6, that are the first viable Xe-bearing compound at Earth’s lower mantle conditions. These new compounds are predicted by extensive crystal structure search in conjunction with ab initio energetic calculations and molecular dynamics simulations. Mass densities and compressional and shear sound velocities calculated at deep-Earth conditions are compatible with pertinent ULVZ and PREM data, thus confirming viability of Xe2FeO2 in geological environments. These results provide compelling evidence for a distinct deep-Earth Xe reservoir beyond previously proposed Xe-Fe and Xe-Ni intermetallic compounds in Earth’s inner core, thereby greatly expanding the range and scope of Xe-bearing compounds in deep Earth. The Xe-Fe oxides may enrich the understanding of prominent geophysical and geochemical processes, such as seismic anomalies near the CMB and possibly new chemical reactions inside Earth’s lower mantle.


Structural predictions

Our structure search is based on a global optimization of free-energy surfaces using the CALYPSO methodology46,47, which has been successfully employed in predicting a large variety of crystal structures48,49,50,51,52. Evolutionary variable-cell calculations were performed at 120, 150, and 200 GPa with 1, 2, 3, and 4 formula units (f. u.) per cell. Most searches converge in 50 generations with about 2500 structures generated.

Ab initio calculations

First-principles total-energy and electronic property calculations were carried out using the density functional theory with the Perdew–Burke–Ernzerhof exchange-correlation functional in the generalized gradient approximation (GGA)53,54 as implemented in the VASP code55, adopting frozen-core all-electron projector-augmented wave method56 with 3s2 3p6 3d7 4s1, 2s2 2p4, and 4d10 5s2 5p6 treated as valence electrons for Fe, O, and Xe, respectively. Correlation effects among the Fe 3d electrons were treated in the GGA + U approach57,58, adopting the recently proposed on-site Coulomb interaction U = 5.0 eV and a Hund’s coupling J = 0.8 Ev36,59,60,61. The spin-polarized and magnetic states were considered in obtaining the total-energy of the compounds containing iron. Zero-point energy was included in all reported calculations. A cutoff energy of 1200 eV for the plane-wave expansion and fine Monkhorst-Pack k meshes62 were chosen to ensure enthalpy convergence of better than 1 meV/atom.

Phonon calculations

To determine the dynamical stability, we performed phonon calculations by the direct supercell method using the Hellmann-Feynman theorem, as implemented in Phonopy code63. The harmonic interatomic force constants are calculated by 3 × 3 × 3 and 3 × 2 × 2 supercells for P21/c-Xe2FeO2 and P−1-XeFe3O6, respectively. Forces were calculated for atomic displacements of 0.01 Å, with a convergence threshold of 1 × 10−5 eV/Å.

Van der Waals interaction

To examine the contribution of vdW interaction to the lattice energy, we have calculated the enthalpy of formation of Xe2FeO2 at high pressures using the vdW-DF2 density functional64. Our results show that the enthalpy of formation is less sensitive to the contribution of vdW correction at high-pressure conditions for Xe-FeO2 compounds, e.g., about 0.6 meV/atom for P21/c Xe2FeO2 at 135 GPa, thus vdW interaction is not considered in the calculations of lattice energy.