Non defect-stabilized thermally stable single-atom catalyst


Surface-supported isolated atoms in single-atom catalysts (SACs) are usually stabilized by diverse defects. The fabrication of high-metal-loading and thermally stable SACs remains a formidable challenge due to the difficulty of creating high densities of underpinning stable defects. Here we report that isolated Pt atoms can be stabilized through a strong covalent metal-support interaction (CMSI) that is not associated with support defects, yielding a high-loading and thermally stable SAC by trapping either the already deposited Pt atoms or the PtO2 units vaporized from nanoparticles during high-temperature calcination. Experimental and computational modeling studies reveal that iron oxide reducibility is crucial to anchor isolated Pt atoms. The resulting high concentrations of single atoms enable specific activities far exceeding those of conventional nanoparticle catalysts. This non defect-stabilization strategy can be extended to non-reducible supports by simply doping with iron oxide, thus paving a new way for constructing high-loading SACs for diverse industrially important catalytic reactions.


Heterogeneous catalysis is pivotal to the modern chemical industry1, with many heterogeneous catalysts comprising transition metals deposited over a solid support phase2. A recent evolution in this field is the dispersion of isolated, individual metal atoms over the support to form single-atom catalysts (SACs)3. Such SACs have attracted considerable attention as a new frontier in heterogeneous catalysis4,5, affording enhanced precious metal thrifting6 and atom economy7,8,9, improved active site homogeneity10,11,12, and the ability to tune the metal-support interface with unprecedented control13,14,15,16, resulting in superior catalytic activity17,18,19,20 and/or high selectivity21,22,23. A diverse range of supports are known to stabilize isolated metal atoms, notably through pinning at electronic and/or structural defects associated with coordinatively unsaturated sites (CUS) by experimental and density functional theory (DFT) studies (Supplementary Appendices I and II)24,25,26,27,28,29,30,31,32,33. The concentration of atomically-dispersed metal atoms, and their stability, are therefore intrinsically linked to the density and stability of defects as described in recent reviews (Supplementary Appendix III)34,35. However, it is extremely difficult to create a high density of thermally stable support defects36, and hence the fabrication of high metal loading SACs remains currently a formidable challenge.

Here we report the discovery that single metal atoms can be stabilized through a strong covalent metal-support interaction (CMSI) that is not associated with surface defects, enabling the genesis of high concentrations of thermally stable single atoms, even on low-surface-area materials. In situ genesis of ferric oxide supported Pt SAC from Pt nanoparticles (NPs) is verified in methane combustion reaction, one of the primary means of human energy production and important for mitigating environmental challenge associated with CH4 emission. Experimental and DFT studies demonstrate that metal oxide reducibility dictates the ability of a support to anchor isolated Pt atoms: α-Fe2O3 favors atomically dispersed Pt, whereas Al2O3 favors NP sintering. However, the non defect-stabilization strategy can be extended to non-reducible oxide by simply doping with iron oxide. This finding provides a promising method to fabricate high-metal-loading SACs with excellent thermal stability.


Co-precipitation prepared thermally stable Pt1/FeOx

A 1.8 wt% Pt/FeOx catalyst was first prepared by co-precipitation (the synthesis details are in the Methods section), denoted as Pt1/FeOx, and subsequently calcined at 800 °C in air for 5 h, denoted as Pt1/FeOx-C800. Aberration-corrected high-angle annular dark-field scanning transmission electron microscopy (AC-HAADF-STEM) with sub-angstrom resolution was used to compare the nature of platinum species between these two materials. In neither case were Pt nanoclusters or NPs observed (Supplementary Figures 1 and 2). Pt1/FeOx comprised isolated Pt atoms dispersed on the FeOx support with some Pt atoms exactly aligned with the Fe atomic columns (Fig. 1a–b). Corresponding CO diffuse reflectance infrared Fourier transform spectroscopy (DRIFTS) of Pt1/FeOx (Supplementary Figure 1c) shows a coverage-independent band at ~2089 cm−1 and the absence of bridged adsorption of CO band (~1860 cm−1), which is consistent with the CO linearly bound to isolated Pt atoms3. Note that our CO infrared bands are broader than those recently reported by Christopher and co-workers37. However, this is unsurprising because in their work ultra-dilute (0.05 wt%) Pt loadings were used to immobilize only one Pt atom per 5 nm monodispersed anatase nanocrystal. Such low loadings favor the population of only the most reactive titania surface sites, and hence a homogeneous local environment. Platinum sintering was not observed following 800 °C calcination by either AC-HAADF-STEM (Fig. 1c–d and Supplementary Figure 2a–b), or powder X-ray diffraction (Supplementary Figure 2c) analysis of the Pt1/FeOx-C800 sample. X-ray absorption spectroscopy (XAS) studies provide further evidence for the complete dispersion of Pt atoms. Figure 1e presents the Fourier transform radial distribution functions of k3-weight extended X-ray absorption fine structure (EXAFS) spectra for Pt1/FeOx before and after calcination. Similar to our previous reports3, no Pt–Pt bond contribution was found. This observation is in marked contrast to the significant sintering typically noted for small metal species/atoms sintered to calcination at elevated temperature38,39, and indicates a very strong interaction between Pt atoms and Fe2O3 that inhibits migration and sintering of the former. X-ray absorption near edge structure (XANES) measurements confirmed that the chemical state of Pt atoms before and after calcination resembled that PtO2 with tetravalent Pt(IV) (Supplementary Figure 2d) rather than metallic platinum with zerovalent Pt(0)3.

Fig. 1

Structure of Pt1/FeOx. a, b AC-HAADF-STEM images of Pt1/FeOx, and c, d Pt1/FeOx-C800, highlighting atomically dispersed Pt (circled in b). 5 nm scale bar for panel a, and 2 nm scale bars for b, c, d. e Fourier transform radial distribution function of the Pt LIII-edge k3-weighted EXAFS spectra of Pt1/FeOx before and after calcination in comparison with PtO2 and Pt foil

Pt NP-generated high loading Pt SACs on Fe2O3 support

Pt NPs are known to liberate mobile PtO2 species at elevated temperature under an oxidizing atmosphere40, which may be subsequently trapped by either larger Pt NPs (Ostwald ripening) or unique oxide sites or crystalline facets resulting in metal dispersion41,42,43,44,45. In the present case, wherein a strong interaction between Pt atoms and the Fe2O3 support is apparent, we anticipate that Pt atoms vaporized from a NP could be trapped and stabilized by the Fe2O3 surface. To test this hypothesis, pre-formed colloidal Pt NPs were supported on Fe2O3 at a 0.3 wt% loading and the ethylene glycol stabilizer was removed by a 500 °C calcination (denoted as 0.3Pt/Fe2O3-NP), prior to various high-temperature calcination treatments. HAADF-STEM imaging revealed the presence of 2–3 nm diameter Pt NPs (Supplementary Figure 3a–b). In contrast to Pt1/FeOx materials, CO DRIFTS of 0.3Pt/Fe2O3-NP exhibited both bridging (1839 cm−1) and coverage dependent linear bound CO (2072–2064 cm−1) (Supplementary Figure 3c), which is consistent with extended arrays of Pt atoms. Higher temperature calcination (800 °C, 5 h) resulted in the complete disappearance of these Pt NPs (denoted as 0.3Pt/Fe2O3-C800, Supplementary Figure 4a), and concomitant formation of a very high density of isolated Pt atoms (Supplementary Figure 4b). Fig. 2 presents the Fourier transform radial distribution function of the Pt LIII-edge k3-weighted EXAFS spectrum of 0.3Pt/Fe2O3-C800, alongside reference distribution functions for Pt foil and PtO2 (corresponding EXAFS spectra and fits appear in Supplementary Figure 5 and Supplementary Table 1). Two prominent scattering distances are observed for 0.3Pt/Fe2O3-C800 at ~1.7 Å and 2.7 Å attributed to Pt–O and Pt–Fe contributions3,27, respectively, confirming only the sole presence of atomically-dispersed Pt atomic species.

Fig. 2

X-ray absorption spectroscopy of the 0.3Pt/Fe2O3-C800 catalyst. Fourier transform Pt LIII-edge radial distribution functions of the 0.3Pt/Fe2O3-C800 catalyst in comparison with PtO2 and Pt foil

Note that some Pt NPs remained visible by electron microscopy after a lower temperature (600 °C) calcination, albeit more loosely coordinated to the underlying support (Supplementary Figure 4c). An oxidizing atmosphere was critical to observe this high-temperature dispersion; annealing 0.3Pt/Fe2O3-NP under Ar at 800 °C promoted Pt aggregation into larger 3–5 nm particles (Supplementary Figure 4d). This observation strongly implicates oxidized Pt species in Pt NP dispersion (Fig. 3), and indeed X-ray photoelectron spectra (XPS) (Supplementary Figure 6c) provide direct evidence for high-valent (near + IV) Pt in the 0.3Pt/Fe2O3-C800 catalyst. This is quite different from those divalent (+II) Pt ions dominating on CeO2 support after high-temperature calciantion46,47, and hence further evidences a stronger Pt-Fe2O3 interaction that partially arises from covalent bonding interaction48,49. Three requirements emerge for the successful conversion of Pt NPs into atomically dispersed Pt: a high temperature to promote Pt mobility; the presence of molecular O2 to partially oxidize the surface of Pt NPs, thereby enabling vaporization of (mobile) PtO2; and a strong interaction between support and surface Pt atoms. Consequently, highly stable static single atoms on heterogeneous surface can be fabricated50.

Fig. 3

Illustration of thermally induced Pt nanoparticle restructuring. a, b Calcination under oxygen, or under an inert atmosphere (c), resulting in dispersion as single-atoms or particle sintering, respectively

The first condition is met for H2PtCl6 functionalized α-Al2O3 (Supplementary Figure 7a–b) subjected to the same high-temperature processing. However, in this case the weak metal-support interaction favors Ostwald ripening and the growth of large (10~50 nm) Pt particles (Supplementary Figure 7c–d) over their dispersion, as previously reported42. Since the particle size in the fresh sample ranges from 2–20 nm (Supplementary Figure 7b), and the dynamics of Pt NP dispersion into Pt atoms are related to particle size51, a control experiment was further performed, in which 2–3 nm Pt NPs were deposited over Al2O3 (Supplementary Figure 7e–f). Sintering was again observed after heat treatment (Supplementary Figure 7g–h), confirming a weak interaction between alumina and Pt species. We note that dispersion of < 1 nm Pt NPs was recently reported over MCM-2251, which may reflect restricted migration of Pt species through the microporous zeolite network.

Having identified conditions under which Pt NPs can be dispersed over an Fe2O3 surface, we explored the effect of Pt loading with a view to maximizing the density of isolated atoms achievable, and thereby compensate for the extremely low surface area (only 5–10 m2 g−1) of the Fe2O3 support after the requisite 800 °C calcination. A higher 1 wt% loading of the same 2–3 nm Pt NPs (denoted as 1Pt/Fe2O3-NP) were also fully transformed into isolated atoms by calcination at 800 °C (Supplementary Figure 8a–b). Low energy ion scattering (LEIS) evidenced a clear decrease in the Pt:Fe atomic ratio in the outermost surface layer upon calcining the stabilizer free 1Pt/Fe2O3-NP to 800 °C (Supplementary Figure 9). Since the total Pt loading determined by inductively coupled plasma spectrometry-atomic emission spectrometry (ICP-AES) remained unchanged, it appears that some Pt atoms diffuses into the near sub-surface region of the Fe2O3 support, possibly by a cation-exchange process52,53. However, a further increase in Pt loading to 2 wt% resulted in the formation of Pt clusters alongside isolated atoms (Supplementary Figure 8c–d), in line with the theoretical maximum loading (~1.5 wt% for Fe2O3 possessing a surface area of 10 m2 g−1, see Methods). A high density of clusters and few single isolated atoms were observed for a 4.5 wt% Pt loading (Supplementary Figure 8e–f). The maximum concentration of atomically-dispersed Pt loading is clearly dictated by the very low support surface area. The emergence of Pt clusters for loadings ≥2 wt% confirms that any Pt atoms diffusing into the support must be confined to the immediate subsurface region and not migrated into the bulk Fe2O3 lattice, since the latter pathway would enable isolated atoms to remain the dominant surface species at far higher Pt loadings.

Disintegration of Pt NPs during high-temperature calcination was directly visualized by in situ HAADF-STEM, and one Fe2O3 crystal of 1Pt/Fe2O3-NP sample was randomly picked to observe the process. Prior to calcination, about 300 Pt particles were visible across the Fe2O3 support, and the average particle size was about 3 nm (Fig. 4a–c). However, after heating to 800 °C under a flow of 1 bar O2 for 20 min, the total number of Pt NPs decreased to ~200, since many of the 2–3 nm Pt NPs shrank and/or disappear entirely, while a few larger particles (size above 10 nm) remained (Fig. 4b–c versus Fig. 4e–f). The loss of small clusters was confirmed by higher resolution, time-resolved imaging (Fig. 4g–i taken from the Supplementary Movie 1), which reveal smaller Pt clusters (e.g., particle 1) disintegrated in less than 35 s, while larger Pt clusters (e.g., particle 2) vanished in 45 s. Previous reports suggest that smaller metal crystallites disperse as adatoms, which migrate towards neighboring (larger) particles and eventually coalesce at elevated temperature via Ostwald Ripening, driven by lowering of the total surface energy54. In this case, however, particle disappearance occurs in the absence of such coalescence, consistent with the accompanying genesis of atomically-dispersed Pt entities.

Fig. 4

In situ characterization of Pt NP oxidative dispersion. ac HAADF-STEM images and size distribution histogram of 1Pt/Fe2O3-NP before, and df after in situ calcination at 800 °C under 1 bar flowing O2 for 20 min: the yellow squares in panels a and d show the same sample area. A 50 nm scale bars in a, d and 10 nm scale bars in b, e. Yellow circles in panel b highlighted the particles missing after calcination for 20 min. gi Sequential HAADF-STEM images from the same area showing the dissociation of small particles (labeled by purple and yellow circles) during in situ calcination: 5 nm scale bars; elapsed time (in seconds) indicated in upper right corner of each image

DFT Studies

The preceding electron microscopy, X-ray spectroscopy and diffraction, and CO chemisorption measurements provide both clear evidence of, and insight into the driving force for, the formation of atomically-dispersed Pt following high-temperature calcination; NP dispersion is triggered by the formation of PtO2 (Supplementary Figure 6). Computational modeling via DFT calculations (Fig. 5a–b) suggests that the evaporation free energy of PtO2 (the dominant surface species under an oxidizing environment) from a Pt(221) step (model in Supplementary Figure 10) is about −0.61 eV per PtO2 at 800 °C, whereas the evaporation energy of Pt1 (the dominant species under inert environments, Supplementary Figure 4d) can reach as high as 4.00 eV, and hence is energetically strongly disfavoured due to CMSI of Pt1 to the surface atoms. By comparison, PtO2 evaporation at 600 °C is virtually thermo-neutral or slightly endothermic (0.07 eV), indicating the critical role of temperature in dispersing Pt NPs. This result is consistent well with the experimental results that the dispersion of NPs only occurred with calcination >600 °C (Fig. 3, Supplementary Figures 4a–c).

Fig. 5

Optimized structures and energy profiles for Pt NP dispersion as isolated Pt atoms. a, b Calculated energies and surface structures for evaporation of a single Pt atom (Pt1) from a Pt(221) step (red value) or evaporation of a PtO2 species from an oxygen pre-covered Pt(221) step (black values). c, d Calculated energies and surface structures for dissociative capture of PtO2 over Fe2O3(0001) surface and concomitant formation of a Pt1 atom and evolved O2. Color code: outermost layer Pt (green); second layer Pt (blue); O (red); Fe (purple)

This temperature-dependent evolution of PtO2 dissociation energetics from a Pt(221) step (representative of the partially oxidized surface of Pt NPs following high-temperature calcination) mirrors that of the catalytic activity for methane oxidation, as discussed below. The dissociative adsorption of PtO2 on an oxygen terminated Fe2O3(0001) surface (and concomitant desorption of one O2 molecule) is highly exothermic at 800 °C (calculated as −2.46 eV, Fig. 5c–d), with PtO2 dissociative capture even more favorable at lower temperature. Note that the evaporation, migration, and trapping do not require the presence of anion or cation vacancies on the support: no Lewis acid sites were detected on the Fe2O3 support by NH3 temperature-programmed desorption, suggesting that Fe2O3 possessed negligible oxygen anion defects following a high-temperature calcination. Therefore, Pt atoms disperse across the ferric oxide support where they are anchored as isolated atoms through a strong local surface interaction. Calculations indicate that these reactively-formed Pt atoms coordinate with four surface oxygen atoms in a distorted square geometry with an average Pt–O length of 1.94 Å, intermediate between that in gas PtO2 (CN = 2, 1.70 Å) and bulk PtO2 (CN = 6, 2.04 Å). Bader charge analysis of an isolated Pt atom on Fe2O3(0001) shows a charge of + 1.43 |e|, approximating to but slightly lower than the charge of Pt in gas PtO2 and bulk PtO2 (Supplementary Table 2), consistent with tetravalent Pt and the XPS analysis (Supplementary Figure 6). The total free energy change for the formation of Fe2O3 stabilized isolated Pt atoms from Pt NPs is −3.07 eV per Pt atom at 800 °C, i.e. such a dispersion is strongly exothermic with low barrier. In comparison, Pt only interacts very weakly (low endothermic free energy) with an alumina surface (Supplementary Figures 1113, Supplementary Table 3). By comparing the charge density difference of Pt1/Fe2O3(0001) and Pt1/Al2O3(010), defined as Δρ = ρPt+slab − ρslab − ρPt, four strong chemical bonds are observed between Pt and adjacent O atoms by covalent (d-p) orbital interactions at the Fe2O3 surface. In contrast, only very weak Pt–O interactions occur at the Al2O3 surface, resulting in Pt–O bond lengths much longer than that on Fe2O3. Bader analysis indicates that each Pt possesses a −0.14 |e| charge, i.e. approximately metallic character (Supplementary Table 2); both findings are attributed to the irreducibility of Al3+, i.e. strong non-redox Al–O bonding network, which prevents any significant metal-support interaction. DFT calculations are hence in excellent agreement with experimental observations. The finding of the stability of SAC closely related to the reducibility of the support is consistent with previous work as well55.

Catalytic performance in methane combustion

The impact of oxygen-induced restructuring at elevated temperature on catalytic performance is striking (Fig. 6). As the reaction temperature of 1Pt/Fe2O3-NP under an oxygen-rich methane gas feed was raised from 300 to 700 °C, the combustion activity increased such that a modest ~18 % conversion was initially attained. However, in contrast to most catalytic reactions wherein activity subsequently decreases with time-on-stream, the activity of 1Pt/Fe2O3-NP displayed a monotonic increase over the following 4 h at 700 °C to reach 65 % conversion. Post-reaction catalyst characterization confirmed that this high-temperature catalyst activation was accompanied by the disappearance of Pt NPs present in the as-prepared material (Fig. 6 left inset), and formation of atomically-dispersed Pt (Fig. 6 right inset, Supplementary Figure 14a–b), demonstrating a causal relationship between in situ genesis of a Pt SAC and dramatically enhanced performance. Note that pre-activation of 1Pt/Fe2O3-NP by calcination at 700 °C for 5 h prior to methane addition resulted in an extremely stable Pt SAC that maintained similar activity for > 16 h on-stream (Supplementary Figure 14c). Since the mass of 1Pt/Fe2O3-NP catalyst (and Pt loading) in this methane light-off experiment is constant, the time-dependent increase in CH4 conversion at 700 °C due to catalyst restructuring is directly proportional to the catalytic activity; single-atom formation induces a four-fold enhancement (18→65 % conversion) in the specific activity. Additional experiments with the same catalyst at 20 % iso-conversion in either its SAC (1Pt/Fe2O3-C700) or nanoparticulate (1Pt/Fe2O3-NP) form confirmed that the specific activity of the former was 4 times greater than that of the latter (2.01 molCH4 h−1 gPt−1 vs. 0.47 molCH4 h−1 gPt−1) and 20 times than that reported for Pt/Al2O356 (Supplementary Table 4). Turnover frequencies based on the number of surface Pt atoms (dispersion) were similar for SAC and nanoparticulate counterparts (0.1 s−1 vs. 0.08 s−1), indicating a common active site, and hence the superior specific activity of the single-atom catalyst reflects its improved atom efficiency (every Pt atom directly activates methane).

Fig. 6

Dynamic formation of a Pt SAC during methane oxidation. Light-off curve of 1Pt/Fe2O3-NP for methane oxidation with a feed gas comprising 0.5 vol% CH4/ 3 vol% O2/ 97 vol% He balance at 30 mLmin-1. STEM images of catalyst before (left-inset) and after (right-inset) reaction. Scale bars, 2 nm. Red square and yellow circles are used to indicate the Pt NP and Pt atoms, respectively

Interaction between Pt atoms and iron-modified support

Fundamental insight into the reaction-induced restructuring of metal NPs over a reducible metal oxide support offers a facile route to synthesize high-loading and thermally stable SACs. Platinum NPs introduced either as pre-formed colloids or e.g. by simple wet impregnation with 1 wt% H2PtCl6 (Supplementary Figure 15a–b) over a low area Fe2O3 support, are readily transformed into isolated Pt atoms by high-temperature calcination (Supplementary Figure 15c–d). Flytzani-Stephanopoulos and co-workers have shown that Na or K ions can stabilize surface hydroxyls, which can in turn stabilize metal (Au and Pt) atoms and/or subnanometer clusters over diverse supports57,58,59. However, our recent work60 has not identified such a role for alkalis, suggesting that Fe2O3 may have unique properties to some degree. To test our hypothesis, we synthesized a sodium-free material using a (NH4)2CO3 precipitant, denoted as Fe2O3(N). Pt NPs exhibited the same dispersion and single-atom formation after 800 °C calcination over this Fe2O3(N) support (Supplementary Figure 16), confirming that the reducible Fe2O3 support, and not presence of Na+, was responsible for stabilizing Pt single-atoms.

The propensity for stabilizing single Pt atoms is dictated by the magnitude of the metal-support interaction, which itself can be tuned by e.g. doping a reducible (Fe2O3) into a non-reducible (Al2O3) oxide (Supplementary Figure 17a) through co-precipitation. As shown in Fig. 7, functionalization of such an Fe2O3-Al2O3 mixed metal oxide by Pt NPs, and subsequent 800 °C calcination, delivers atomically-dispersed Pt precisely as observed over the pure ferric oxide (Supplementary Figure 17b–c), but in a higher area form (~30 m2 g−1).

Fig. 7

Illustration of Pt NP sintering/dispersing on different supports. Metal oxide reducibility dictates the ability of a support to anchor isolated Pt atoms: Fe2O3 favors atomically dispersed Pt, whereas Al2O3 favors nanoparticle sintering. Doping iron oxide into non-reducible support (Fe2O3–Al2O3) can adjust noble metal dispersion


We reported a facile synthesis of thermally-stable Pt SAC that achieved remarkable catalytic performance towards methane combustion. Isolated Pt atoms with high oxidation state are not stabilized by surface defects but through a strong covalent interaction with iron and oxygen atoms on the surface. Since Fe can be simply incorporated into a variety of oxides with low area and/or defect density, e.g. perovskites and spinels, our approach may afford a generic route to fabricate high loading Pt SACs over diverse supports being able to operate under harsh reaction conditions.


Synthesis of FeOx and Fe2O3

Ferric nitrate (Fe(NO3)3·9H2O), 98%, Sigma-Aldrich) and sodium carbonate (Na2CO3, 99.5% Sigma-Aldrich) were used as purchased. An aqueous solution of Fe(NO3)3 (1 mol L−1) was obtained by dissolving Fe(NO3)3·9H2O (122 g, 0.3 mol) in deionized water (300 mL). FeOx was subsequently prepared from this solution by precipitation. First, Na2CO3 (11 g) was added in water (100 mL) and stabilized at 50 °C in a water bath. To this, 40 mL Fe(NO3)3 solution was slowly added (1 mL min−1) under vigorous stirring at 50 °C for 3 h, and then aged static for a further 2 h. The recovered FeOx solid was washed with deionized water and dried at 60 °C overnight. Fe2O3 was obtained by calcining FeOx at 800 °C (ramp rate 3 °C min−1) for 5 h under flowing air (100 mL min−1).

Synthesis of Fe2O3(N)

Ferric nitrate (Fe(NO3)3·9H2O), 98%, Sigma-Aldrich) and ammonium carbonate (Sigma-Aldrich, (NH4)2CO3 99.5%) were used as purchased. First, (NH4)2CO3 (4 g) was added in water (6 mL) and stabilized at 50 °C in a water bath. To this, 20 mL Fe(NO3)3 solution(1 mol L−1) was slowly added (1 mL min−1) under vigorous stirring at 50 °C for 3 h, and then aged static for a further 2 h. The recovered FeOx solid was washed with deionized water and dried at 60 °C overnight. Fe2O3(N) was obtained by calcining FeOx at 800 °C (ramp rate 3 °C min−1) for 5 h under flowing air (100 mL min−1) to obtain the Na+-free support.

Synthesis of Fe2O3–Al2O3

An Fe2O3-Al2O3 mixed oxide was synthesized by co-precipitation. Fe(NO3)3·9H2O (8 g, 0.02 mol) and Al(NO3)3·9H2O (7.5 g, 0.02 mol, 98%, Sigma-Aldrich) were first dissolved in 80 mL deionized water. Separately, (NH4)2CO3 (7.7 g, 0.08 mol, 99%, Sigma-Aldrich) was dissolved in 80 mL deionized water. The two aqueous solutions were combined in 30 mL water at 50 °C under stirring for 3 h, and then aged static for a further 2 h. The resulting solid was recovered by filtration, washed with deionized water, dried at 60 °C overnight, and finally calcined at 800 °C (ramp rate 3 °C min−1) for 5 h under flowing air (100 mL min−1).

Synthesis of Pt1/FeOx and Pt1/FeOx-C800

Pt1/FeOx was prepared by co-precipitation of an aqueous mixture of chloroplatinic acid (H2PtCl6·6H2O, 37 mgPt mL−1, 2.6 mL, 99.9%, Sigma-Aldrich) and Fe(NO3)3·9H2O (1 mol L−1, 40 mL) with Na2CO3 solution (11 g Na2CO3 in 100 mL H2O) at 50 °C under stirring for 3 h, and ageing static for a further 2 h. The resulting solid was recovered by filtration, washed with deionized water and dried at 60 °C overnight. A portion of the Pt1/FeOx was then calcined as above at 800 °C and denoted as Pt1/FeOx-C800. The Pt loading determined by ICP was 1.8 wt%.

Synthesis of xPt/Fe2O3-NP and xPt/Fe2O3-C800

Pt nanoparticles (NPs) were synthesized according to the literature61. Typically, an ethylene glycol solution of NaOH (0.5 mol L−1) was added into an ethylene glycol solution of H2PtCl6·6H2O under stirring (3.7 mgPt mL−1). The resulting transparent yellow platinum colloidal solution was heated at 160 °C for 3 h under flowing Ar to form a transparent dark-brown platinum colloidal solution. Separately, Fe2O3 was dispersed in deionized water by sonication, to which the Pt NP colloidal solution was added, and the resulting solid dried overnight at 100 °C, and then calcined at 500 °C for 5 h under flowing air to remove the glycol stabilizer. A series of Pt NP catalysts were prepared with different Pt loadings, denoted as xPt/Fe2O3-NP (x = 0.3, 1, 2, or 4.5 wt% Pt as determined by ICP). xPt/Fe2O3-C800 was obtained by treating xPt/Fe2O3-NP under flowing air (100 mL min−1) at 800 °C for 5 h.

Synthesis of Pt/Al2O3-NP and Pt/Al2O3-C800

Pt/Al2O3-NP was prepared following the above procedure by dispersing colloidal Pt over the Al2O3 support at a Pt loading of 0.3 wt% as determined by ICP, and then calcined at 300 °C for 5 h under flowing air. Pt/Al2O3-C800 was obtained by treating Pt/Al2O3-NP under flowing air (100 mL min−1) at 800 °C for 5 h.

Synthesis of Pt/Fe2O3–Al2O3-NP and Pt/Fe2O3–Al2O3-C800

Pt/Fe2O3–Al2O3-NP and Pt/Fe2O3–Al2O3-C800 were prepared following the above procedure by dispersing colloidal Pt over the Fe2O3–Al2O3 support at a Pt loading of 0.5 wt% as determined by ICP.

Synthesis of 0.3Pt/Fe2O3-C600 and 0.3Pt/Fe2O3-Ar800

0.3Pt/Fe2O3-C600 was obtained by treating 0.3Pt/Fe2O3-NP under flowing air (100 mL min−1) at 600 °C for 5 h. 0.3Pt/Fe2O3-Ar800 was obtained by treating 0.3Pt/Fe2O3-NP under flowing Ar (100 mL min−1) at 800 °C for 5 h.

Synthesis of H2PtCl6/Fe2O3 and H2PtCl6/Fe2O3-C800

In a typical procedure, 1 g Fe2O3 was dispersed in 5 mL deionized water by sonication, to which 0.3 mL H2PtCl6 aqueous solution (37 mgPt mL−1) was added. Water was gradually evaporated by heating the resulting suspension at 80 °C. The resulting solid was calcined at 300 °C for 5 h under flowing air (100 mL min−1) and denoted as H2PtCl6/Fe2O3. The Pt loading was 1 wt% as determined by ICP. A portion of H2PtCl6/Fe2O3 was also heated at 800 °C under flowing air (100 mL min−1) for 5 h to generate H2PtCl6/Fe2O3-C800.

Synthesis of H2PtCl6/Fe2O3(N) and H2PtCl6/Fe2O3(N)-C800

In a typical procedure, 150 mg Fe2O3(N) was dispersed in 2 mL deionized water by sonication, to which 0.013 mL H2PtCl6 aqueous solution (37 mgPt mL−1) was added. Water was gradually evaporated by heating the resulting suspension at 80 °C. The resulting solid was calcined at 300 °C for 5 h under flowing air (100 mL min−1) and denoted as H2PtCl6/Fe2O3(N). The Pt loading was 0.2 wt% as determined by ICP. A portion of H2PtCl6/Fe2O3 was also heated at 800 °C under flowing air (100 mL min−1) for 5 h to generate H2PtCl6/Fe2O3(N)-C800.

Synthesis of H2PtCl6/Al2O3 and H2PtCl6/Al2O3-C800

α-Al2O3 (99.5%, Sigma-Aldrich) was used as purchased. H2PtCl6/Al2O3 and H2PtCl6/Al2O3-C800 were prepared following the above procedure by dispersing H2PtCl6 over the α-Al2O3 support. The Pt loading was 1 wt% as determined by ICP.


Pt loadings were determined by inductively coupled plasma spectrometry-atomic emission spectrometry (ICP-AES) on an IRIS Intrepid II XSP instrument (Thermo Electron Corporation). X-ray diffraction (XRD) patterns were collected on a PW3040/60 X'Pert Pro super (PANalytical) diffractometer, operating at 40 kV and 40 mA using a Cu Kα radiation source (λ = 0.15432 nm) with a scanning angle (2θ) of 10–80°. In situ diffuse reflectance infrared Fourier transform spectra (DRIFTS) were collected at 25 °C with a Bruker Vertex 70 spectrometer equipped with a mercury cadmium telluride (MCT) detector at a resolution of 4 cm−1 over 32 scans. Samples were first heated in situ at 200 °C under flowing He for 0.5 h, then cooled to room temperature prior to recording of background spectra. Subsequently, a 1 vol% CO/He flow was introduced to the sample for 10 min. The environmental cell was then purged with flowing helium to remove gas phase CO, prior to spectral acquisition of chemisorbed CO species. Temperature-programmed desorption (TPD) was conducted on a Micromeritics AutoChem II 2910 automatic catalyst characterization system equipped with a mass spectrometer. First, the Fe2O3 support was loaded into a U-shape quartz reactor and pretreated at 200 °C in He for 0.5 h to remove adsorbed hydrates and carbonates. After cooling to 60 °C, NH3 gas pulses were injected until a stable signal was obtained, and the sample then heated to 900 °C under He at 10 °C min−1. Synchrotron radiation experiments were performed at BL14B2 of SPring-862 and BL14W1 of the SSRF light sources. Pt LIII-edge transmission X-ray absorption spectra were acquired on samples loaded into the Al2O3 tube, in addition to Pt foil and PtO2 powder references. Spectra were background subtracted, normalized, and fitted using the IFEFFIT software suite63. X-ray photoelectron spectra (XPS) were performed on a VG ESCALAB MK2 apparatus using Al Kα radiation (1486.6 eV, 12.5 kV, 250 W) to obtain the binding energies and oxidation states of Pt. Binding energies are referenced to adventitious carbon at 284.8 eV. High-angle annular dark-field scanning transmission electron microscopy (HAADF-STEM) images were obtained on a JEOL JEM-2100F. Aberration-corrected HAADF-STEM images were obtained on a JEOL JEM-ARM200F equipped with a CEOS probe corrector. Samples were dispersed by ultrasonication in ethanol, and the resulting solution dropped on to carbon films supported on copper grids. In situ imaging was performed on a Titan Cubed Themis G2 300 microscope using a DENSsolutions Climate S3 and Gas flow and Heating System, which comprised a heated sample holder and gas delivery manifold. The sample was mounted in a 5 μm gap between two 30 nm thick SiN windows. The oxygen purity used for the in situ calcination experiment was 99.999%. Reported temperatures were based on the DENSsolutions calibration. Low energy ion scattering (LEIS) spectra were acquired on a Kratos AXIS Supra spectrometer using 1 keV He+ ions generated from a Minibeam 6 Gas Cluster Ion Source, at a scattering angle of 130 °, and 320 eV analyzer pass energy, averaged over a sample area of 500 μm2.

Catalytic evaluation

CH4 oxidation was performed in a U-shaped quartz reactor using 20 mg catalyst and a feed gas comprising 0.5 vol% CH4, 3 vol% O2, and 97 vol% He balance at 30 mL min−1. The effluent gas composition was analyzed by an on-line Agilent 6890 A gas chromatograph equipped with a TDX-01 column and a thermal conductivity detector. CH4 conversion was calculated based on the difference between inlet and outlet concentrations.

Turnover frequency (TOF) calculation

TOFs were calculated from specific activities measured at 700 °C and approximately 20 % CH4 iso-conversion for 17 mg 1Pt/Fe2O3-NP and 6 mg 1Pt/Fe2O3-C700 catalysts respectively. A common gas flow rate of 50 mL min−1 was used, resulting in a space velocity of 176,000 mL h−1 gcat−1 for 1Pt/Fe2O3-NP and 500,000 mL h−1 gcat−1 for 1Pt/Fe2O3-C700. The Pt dispersion of 1Pt/Fe2O3-NP was calculated according to the following relationship between the dispersion (D) and particle radius (r): D / % = 100*5.6/rPt. The average particle radius of 1Pt/Fe2O3-NP was 15 Å (Fig. 4c), corresponding to a dispersion of 30 %, while that for 1Pt/Fe2O3-C700 was 100 %. TOFs were calculated by normalizing specific activities to the product of the dispersion and total Ptmols (identical for both catalysts).

DFT parameters

All DFT + U calculations were performed using spin-polarized density functional theory (DFT) with the generalized gradient approximation (GGA) and Perdew-Burke-Ernzerhof (PBE) exchange-correlation functional as implemented in VASP5.3.564,65,66. The U-J value of 3.0 eV was used to describe the strong correlation of the localized Fe 3d states3,67,68. Valence states of all atoms were expanded in a plane wave basis set with a cutoff energy of 400 eV, and a Monkhorst-Pack mesh of 3 × 3 × 1 k points was used for Brillouin Zone integration. Atomic positions were optimized by the conjugate gradient algorithm until forces were < 0.02 eV/Å. Free energy changes were calculated from zero-point energies, enthalpies, and entropies of gas Pt single atom and PtO2 species corrected at 600, 700 and 800 °C, respectively as summarized in Supplementary Table 3.

Computational models

A Pt(221)-p(3 × 1) surface slab was used to model the step and edge of Pt NPs (coordination number = 7 for atoms at edges). We applied periodic models of surface slabs with five atomic layers, with the bottom two layers frozen and the remaining layers allowed to relax. The (0001) surfaces of α-Fe2O3-p(2 × 2) were also represented by a periodic slab model. Antiferromagnetic properties of α-Fe2O3 were represented by a ( + – – + ) magnetic configuration, which was previously proven to be most energetically favorable for α-Fe2O33. We chose slabs containing 9 layers of Fe atoms and 5 atomic layers of O to model the O-terminated surface. The bottommost Fe–O layers were frozen during geometry optimization. A θ-Al2O3(010)-p(4 × 2) surface slab was used to model the alumina substrate, consisting of six O–Al layers, wherein the bottom two O−Al layers were frozen while the remaining layers were allowed to relax69,70. The IDIPOL tag was set to 3 to switch on dipole corrections to the total energy along the z-direction. All supercell slabs were periodically repeated with a 15 Å vacuum layer between surfaces in the direction of the surface normal.

Theoretical maximum loading of dispersed Pt atoms over Fe2O3 support

The BET surface area of Fe2O3 was 5–10 m2 g−1, hence 1 g of Fe2O3 provides ~5–10 m2 of surface (S). Our DFT calculation model indicates that the maximum density of atomically dispersed Pt (D) is 4.5 atom nm−2. The total number of isolated Pt atoms (N) that could be achieved for 1 g of Pt/Fe2O3 is therefore predicted to be N = D × S. Since the mass of Pt (m) equals N/NA × M, where NA is Avogadro’s constant (6.02 × 1023 mol−1), and M is the molar mass of Pt (195 g mol−1), the theoretical maximum loading of isolated Pt atoms that could be dispersed over 1 g of Fe2O3 is m(g)/1(g) × 100 % = (D × S / NA) × M × 100% = 1.5 wt%.

Data availability

The data that support the plots within this paper and other findings of this study are available from the corresponding authors upon reasonable request.


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This paper is dedicated to the 70th anniversary of the Dalian Institute of Chemical Physics, Chinese Academy of Sciences. This work was supported by National Natural Science Foundation of China (21606222, 21573232, 21776270, 21590792, 91645203, 51761165012), National Key Projects for Fundamental Research and Development of China (2016YFA0202801, 2017YFA0700104), Strategic Priority Research Program of the Chinese Academy of Sciences (XDB17020100), and DNL Cooperation Fund, CAS (DNL180403). The synchrotron radiation experiment was performed at the BL14B2 of SPring-8 with the approval of Japan Synchrotron Radiation Research Institute (Proposal No. 2011B1974), Japan, and the BL14W1 at the Shanghai Synchrotron Radiation Facility, Shanghai Institute of Applied Physics, China. We thank Kratos Analytical Ltd, Manchester for LEIS measurements. Financial grant from the China Postdoctoral Science Foundation (2017M621170). DICP Outstanding Postdoctoral Foundation (2017YB02), and dedicated funds for methanol conversion from DICP. J. Luo thanks National Program for Thousand Young Talents of China, Tianjin Municipal Science and Technology Commission (15JCYBJC52600). The authors thank Kai Wang, Mengke Ge and Xingang Hou for their assistance with in situ STEM measurements. The computational work was performed using supercomputers at Tsinghua National Laboratory for Information Science and Technology and Lvliang Tianhe-2 Supercomputing Center.

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R.L. synthesized the catalyst and performed most of the reactions. S.M. performed the electron-microscopy characterization. W.X. and J.Luo performed the in situ electron microscopy. J-C.L. and J.Li did the theoretical calculations and analysis. Y-T.C., X.L. and Lei Li carried out the EXAFS experiment. Lin Li carried out the CO-DRIFT experiment. Y.C. and J.Lin provided reagent. T.L. and F.C. performed some experiments. A.F.L. provided the LEIS data and edited the manuscript. R.L. and B.Q. wrote the manuscript. A-Q.W. and X.W. revised the paper. B.Q. and T.Z. designed the study and supervised the project.

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Correspondence to Jun Luo or Botao Qiao or Jun Li.

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Lang, R., Xi, W., Liu, JC. et al. Non defect-stabilized thermally stable single-atom catalyst. Nat Commun 10, 234 (2019).

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