Concave curvature facets benefit oxygen electroreduction catalysis on octahedral shaped PtNi nanocatalysts

Department of Chemistry, Chemical Eng Berlin, 10623 Berlin, Germany. E-mail: pstr Ernst Ruska-Centre for Microscopy Forschungszentrum Jülich GmbH, 52425 fz-juelich.de ZELMI – Central Facility for Electron Micro Berlin, Germany † Electronic supplementary information including parameters of Rietveld rene and additional results from electrochemic aer electrochemical testing. See DOI: 10 ‡ These authors contributed equally to th Cite this: J. Mater. Chem. A, 2019, 7, 1149


Introduction
Single crystal studies have revealed that the oxygen reduction reaction (ORR) on platinum surfaces is a highly structuresensitive electrocatalytic reaction. 1,2The trend in ORR activity of low-index pure Pt single crystal surfaces in non-adsorbing electrolytes follows the order Pt(100) ( Pt(111) z Pt(110). 3,4kewise, Pt alloy surfaces have demonstrated a sensitive dependence of their catalytic ORR activity on their surface atomic arrangement. 4Most notably, a Pt 3 Ni(111) single crystal facet, prepared in a 700 C annealing process during which a single atom Pt "skin" layer segregated to the top of the surface, exhibited a 10-fold activity improvement over a Pt(111) single crystal facet. 46][7][8][9] Even though all of these studies on octahedral PtNi nanocatalysts closely refer to the ideal Pt 3 Ni(111) single crystal surface with a Pt skin, not even one of these studies actually succeeded in preparing the intended PtNi alloy nano-octahedra with exclusive exposure of {111}-oriented Pt skin layer facets.This is most likely because none of the reported synthetic routes toward nano-octahedra involved thermal annealing at sufficiently high temperatures, where the thermal segregation of a Pt monolayer (the Pt skin) on top of a well-alloyed PtNi crystal would occur.On the other hand, application of a temperature of 700 C, at which this process takes place, would invariably destroy the octahedral shape 10 and, hence, the prevalence of {111} facets.Nonetheless, most of the reported octahedral nanocatalysts featured electrocatalytic ORR activity benets in line or even greatly exceeding the original 10-fold improvement over pure Pt of the structurally well-dened Pt 3 Ni(111) single crystal surface with a Pt skin structure.Evidently, the well-ordered Pt 3 Ni(111) Pt skin surface with its unique electronic and structural arrangements is not the only type of PtNi alloy surface that is able to efficiently catalyze the electroreduction of oxygen. 11Actually, as reported recently, other benecial chemical or structural factors previously overlooked appear to weigh in as well. 12n the present work, we study the inuence of the local atomic structural and compositional order of facets of Ni-rich PtNi nano-octahedra on their electrocatalytic ORR activity.We compare nano-octahedral facets featuring a Pt-concave {111} morphology with compositionally homogeneous and structurally more ideal, at {111} and {100} nano-cuboctahedral facets.
To achieve this, we analyse the structure, and image and element-map the morphology and composition of PtNi nanoparticles aer thermal reductive annealing, and link them to their ORR activity and stability during potential cycling.We argue that like all previous studies, at no point in time, the atomic surface structure of our own nano-octahedra resembles even remotely the originally reported ideal Pt 3 Ni(111) structure with a "Pt skin" overlayer.However, we provide clear evidence that the Pt-enriched, concave {111} facets unfold a highly benecial ORR activity.In contrast, well-annealed smooth alloy facets perform catalytically less active.To explain this nding, we report and discuss a strong correlation between Pt-concave {111} facets and the presence of local microstrain that appears to be a reliable experimentally accessible descriptor for the catalytic activity of PtNi nano-alloy particles.We ultimately conclude that the quest for an ideally ordered Pt 3 Ni nanooctahedron with the original Pt skin structure may be, albeit very challenging, worth pursuing.Our ndings and conclusions show that catalytically equally or even more active nano-alloy facets can be designed using Pt-concave {111} facets.In other words, stepped and highly rough surfaces outperform ideally ordered ones in catalytic performance and tend to be synthetically more accessible.

Synthesis
For the synthesis of octahedral PtNi nanoparticles, 0.2 mmol Pt(acac) 2 and 1.4 mmol Ni(acac) 2 were dissolved in 50 mL DMF by ultrasonication for 5 min.The homogeneous solution was transferred into a glass-lined stainless steel autoclave.The sealed autoclave was heated from room temperature to 130 C within 30 min.The temperature was held for 42 h before it was naturally cooled down to room temperature.Aerwards the particles were supported on carbon (Vulcan XC72R) by 5 min ultrasonication and under around 23 h static conditions at room temperature.Finally, the PtNi/C was washed with ethanol/ water several times and freeze-dried aerwards.This synthesis is based on that reported by Cui et al. 9 For annealing, a furnace tube with a portion of the asprepared sample was purged with nitrogen for 1 h at room temperature.Aerwards, the atmosphere was changed to 4% H 2 /Ar and the temperature was raised at 10 K min À1 to a temperature between 200 and 500 C, and held for 30 min.Aerwards it was cooled down in a nitrogen ow to room temperature.The obtained samples are labeled "H 2 T" with T being the annealing temperature.

Physical and chemical characterization
Inductively coupled plasma-optical emission spectroscopy (ICP-OES) was used for elemental and compositional analysis using a Varian 715-ES spectrometer with a CCD detector.Samples were digested in acid (HNO 3 : H 2 SO 4 : HCl ¼ 1 : 1 : 3) and heated using microwave irradiation to 180 C for 10 min, with a ramping step of 10 min.The samples were diluted with Milli-Q water (>18 MU cm À1 ) to reach appropriate emission intensity.Standards with a known concentration were co-analysed with the samples.
Powder X-ray diffraction (XRD) was carried out on a D8 Advance X-ray diffractometer (Bruker AXS) working with a position sensitive LynxEye detector (PSD) and a Cu K a source.The diffraction patterns of the catalysts were recorded at diffraction angles between 20 and 90 with a step size of 0.05 and a collection time of 10 s.Rietveld renement was performed with Topas 4.2 taking into account the zero error, sample displacement, instrumental broadening, lattice constant and size-and strain-induced Gaussian-/Lorentzian peak broadening.Additionally, a single peak analysis was carried out using MDI Jade 9.
For transmission electron microscopy (TEM), Cu grids with a lacey carbon layer and 300 mesh from Plano GmbH were coated with the dispersed catalyst.The measurements were performed on a FEI Tecnai G 2 20 S-TWIN transmission electron microscope with a LaB 6 cathode operating at an accelerating voltage of 200 kV.
Scanning transmission electron microscopy (STEM) was performed using a FEI Titan 80-200 ("ChemiSTEM") electron microscope with a Cs-probe corrector (CEOS GmbH) and a highangle annular dark eld (HAADF) detector. 13The microscope was operated at 200 kV.In order to achieve "Z-contrast" conditions, a probe semi-angle of 25 mrad and an inner collection semi-angle of the detector of 88 mrad were used.Compositional maps were obtained with energy-dispersive Xray (EDX) spectroscopy using four large-solid-angle symmetrical Si dri detectors.For EDX elemental mapping, Pt L and Ni K peaks were used.The error of the EDX composition measurement is AE2 at%.

Electrochemical characterization
The electrochemical characterization of the catalysts was performed in a three-compartment electrochemical glass cell lled with 0.1 M HClO 4 solution as the electrolyte at room temperature.A Pt mesh and a Hg/Hg 2 SO 4 electrode were used as the counter electrode and reference electrode, respectively, and a commercial rotating disk electrode (RDE) setup from Pine Instruments equipped with a glassy carbon disk (5 mm in diameter) was used.All measurements were controlled using a VSP-5 potentiostat from BioLogic.
Catalyst inks were prepared by dispersing about 5 mg of the catalyst powder in 3.98 mL of Milli-Q water, 1 mL of 2-propanol and 20 mL of Naon solution (5 wt%).The inks were homogeneously dispersed by ultrasonication.To prepare a thin catalytic lm with about 8 mg Pt cm À2 on the GC electrode surface, 10 mL of the prepared ink was drop-cast and the electrode was dried at 60 C for 7 min in air.Cyclic voltammograms were collected in deaerated 0.1 M HClO 4 electrolyte under a nitrogen atmosphere in the voltage range between +0.05 and +1.00 V RHE .For activation, 25 cycles were performed with a scan rate of 100 mV s À1 .The ECSA was obtained using the mean integral charge of the underpotentially deposited hydrogen area as well the desorption area corrected for the capacitive current and Pt pseudo-capacity of 210 mC cm Pt À2 , assuming that one hydrogen atom observed correlates to one platinum atom.For ORR measurements, linear sweep voltammetry (LSV) was performed in an oxygenated 0.1 M HClO 4 electrolyte solution.The polarization curves were recorded by anodic sweeping from +0.05 to +1.00 V RHE with a scan rate of 5 mV s À1 and a rotation speed of 1600 rpm.The intrinsic kinetic current at +0.9 V RHE was corrected for the mass transport diffusion limiting current between +0.2 and +0.6 V RHE .
Stability measurements were performed via potential cycling two times, 4000 cyclesbetween +0.5 and +1.0 V RHE with a scan rate of 50 mV s À1 in N 2 -saturated 0.1 M HClO 4 at 0 rpm.Before and aer each stability protocol, three CVs between +0.05 and +1.0 V RHE at 100 mV s À1 were recorded.ORR activity was measured aer activation (25 CVs), aer 4000 cycles and aer subsequent 4000 ones, i.e. 8000 cycles, of each electrode, using the same conditions as those described above.

Results and discussion
Structural and morphological transformations during thermal annealing Bulk structural analysis.PtNi octahedral shaped nanoparticles with the nominal composition PtNi 1.5 were prepared using a solvothermal, autoclave based synthesis procedure.The unannealed PtNi alloy catalyst (henceforth referred to as "asprepared") with 8 nm mean particle size was subjected to postsynthesis thermal annealing in a hydrogen ow (4 vol% H 2 /Ar mixtures) at temperatures between 200 and 500 C. The resulting catalysts are henceforth labeled "H 2 T", with T being their respective annealing temperature.For all obtained catalyst samples, inductively coupled plasma-optical emission spectroscopy (ICP-OES) analysis revealed no change in the actual atomic Pt : Ni composition of 38 at% Pt and 62 at% Ni or in the actual Pt weight loading on the carbon support (20 wt% Pt) (see Table S1 (ESI †) for details).
The long-range crystalline structure of the catalysts aer annealing was investigated by X-ray diffraction (XRD), and the patterns are depicted in Fig. 1a.All samples exhibited patterns typical of the face centered cubic (fcc) structure type.The comparison with the reections of pure Pt fcc (ICSD 4-0802) and pure Ni fcc (ICSD 4-0850) evidenced the formation of PtNi alloys.Furthermore, the reections of the as-prepared PtNi are rather broad and asymmetric with a tailing on the low-angle side.With increasing annealing temperature, a gradual change in the lattice structure occurred: reections shied to higher angles (see gray dashed lines in Fig. 1a).In addition, all peaks became more symmetric, best visible for the (220) reection.As the elemental composition remained constant, the reection shi directly correlates with lattice structural changes in the bimetallic nano-octahedra.
Rietveld renement of each pattern revealed details of the structural changes upon annealing.The best renement results were obtained using a single fcc disordered PtNi alloy phase, which was modied by interstitial oxygen atoms on the vacant tetrahedral sites with rened occupancy.The inuence of the high surface area carbon support, especially near the alloy (111) reection (Fig. S1, ESI †), was carefully subtracted and corrected for.Accordingly, the Rietveld analysis evidenced phase-pure PtNi alloy nanoparticles with some residual lattice oxygen atoms.Further details of the renement as well as the detailed values of the structural parameters are given in the ESI on page 2 and Table S2, † and two renement deconvolutions are presented in Fig. S2 (ESI †).In Fig. 1b-d, the Rietveld-derived experimental lattice constant a, the microstrain e 0 , and the mean crystallite size are plotted against annealing temperature.Consistent with simplied single peak analyses (see Fig. S3, ESI †), gradual lattice contraction was evident above 200 C.The microstrain e 0 , also referred to as raw microstrain, was obtained from Rietveld renement without any processing.It is generally understood as a measure for local disorder in atomic lattices and is derived from the variation of the lattice parameter around the mean, i.e. inuencing the peak width without a change in its position.5][16] Herein, the evolution of the microstrain displayed a maximum for the H 2 300 C catalyst, while the mean crystallite size (structural coherence length) increased monotonically with annealing temperature starting from the as-prepared sample.Thus, up to 300 C annealing temperature, the microstrain and coherence length of the nanooctahedra exhibited an unusual positive correlation; in other words, the nanoparticles of H 2 200 C and H 2 300 C exhibited more local disorder than that expected from their size.This excess microstrain and its origin will become the subject of our discussion of activity trends below.Starting from 300 C, the microstrain and crystallite size follow their usual inverse relationships (Fig. S4, ESI †).Both the lattice constant and microstrain reached a minimum for the PtNi-500 sample, suggesting a structurally and energetically relaxed alloyed state of the PtNi nanoparticles.Looking at the crystallite size, we can conclude that an increase in the coherence length occurred by annealing at 500 C, while Pt and Ni interdiffusion removed elemental anisotropies leading to more homogeneously alloyed lattices.
Particle ensemble morphology.To cross-correlate the X-ray diffraction derived mean crystallite size with the actual mean nanoparticle size and track morphological changes upon annealing, all samples were investigated by (Scanning) Transmission Electron Microscopy, (S)TEM.Fig. 2A shows the bright-eld (BF) TEM image of the as-prepared PtNi nanoparticle ensemble.Its largely octahedral morphology remained stable to thermal annealing in hydrogen up to 300 C (Fig. 2C) beyond which major morphological transformations set in.This 300 C temperature threshold was also supported by highangle annular dark eld (HAADF) STEM analysis results in Fig. 3K and L (300 C) and Fig. 3P and Q (400 C).Annealing at 400 C caused the octahedral particles to transform into a cuboctahedral shape, which is mainly composed of {111} and {100} facets (Fig. 3Q).As a consequence, the particles appeared rounded in the low magnication images (Fig. 2D and 3P).At 500 C, the octahedral shape was irreversibly lost and nearspherical particles were observed (Fig. 2E).Interestingly, upon annealing, the TEM-based particle size remained essentially constant (Fig. 2F), despite the severe morphological changes aer annealing to 500 Cthe particle size distributions are depicted in Fig. S5 (ESI †).Only a few coalesced particles were formed aer annealing at 400 C and 500 C, which were presumably closely neighboring particles before annealing.The generally maintained particle size explains largely localized Pt atom diffusion and redistribution This journal is © The Royal Society of Chemistry 2019 on each particle.Furthermore, the stark discrepancy between the TEM-derived mean particle size and the XRD-derived crystallite size of the PtNi domains (Fig. 1d) likely suggests the presence of multi-grain particles at least up to 300 C. With higher annealing temperature, the variation of the elemental distribution results in growth and Ni enrichment of the PtNi domains and, thereby, leads to the structural relaxation observed for H 2 500 C.
Elemental anisotropy and particle concavity.To learn more about the local elemental Pt or Ni enrichment and segregation inside the nano-octahedra, STEM-EDX elemental maps were recorded (Fig. 3).The initial as-prepared PtNi nanoparticles appear concave in the Z contrast (Fig. 3A and B).The combined EDX map of such octahedral nanoparticles oriented close to a h110i zone axis (Fig. 3C) indicated the enrichment of Ni in the {111} facets and a Pt-rich frame, evident by a red Pt-rich strip across the center of the nanoparticles.Accordingly, the nanoparticles constitute imperfect Pt octahedra with concave {111} facets (Fig. 3D).Hence, in line with previous work, 17,18 these asprepared octahedral nanoparticles feature an anisotropic elemental distribution of Pt and Ni atoms.We note that the concave shape in the HAADF STEM images of the as-prepared catalyst (Fig. 3A and B) primarily represents the Pt atom distribution (Fig. 3D), due to the much weaker Z-contrast of Ni atoms (we will term this structural feature "Pt-concave" here-aer).However, since segregated Ni atoms "ll" the {111} concave cavities of the particles (Fig. 3E), the facets of the asprepared particles are actual smooth, strongly Ni-enriched ones.Compositional quantication of the as-prepared NPs yielded an average composition of Pt 43 at% and Ni 57 at%, which is in reasonable agreement with the sample-averaged ICP-OES value of Pt 37 at% and Ni 63 at%, considering possible surface dissolution of Ni atoms during the time the NPs were kept in the dispersion prior to the STEM-EDX investigations.The annealed nanoparticles showed an even better agreement between STEM-EDX and ICP-OES compositions (see Table S1, ESI †) suggesting a stabilizing effect of annealinginduced Pt and Ni interdiffusion against Ni dissolution.
The NPs of H 2 200 C showed only slight morphological changes (Fig. 3F) compared to the as-prepared sample, where some individual Pt-concave {111} facets (arrow in Fig. 3B) appeared to transform into somewhat less concave {111} facets (arrow in Fig. 3G).The corresponding EDX elemental maps suggested the migration of Pt atoms from the corner to the initially Ni-enriched {111} facets (arrow in Fig. 3I), while the distribution of Ni is similar to that in the as-prepared state (see Fig. 3J).Accordingly, thermal annealing at moderate temperatures appears to heal Pt-concave {111} facets. 19At the same time, the rearrangement of Pt from vertices to facets is associated with interdiffusion of Pt and Ni atoms in the {111} facets.
The NPs of H 2 300 C retained their octahedral shape with a Pt distribution similar to that of H 2 200 C (Fig. 3L and N), having distinct Pt-concave {111} facets.Fig. 3O shows that Ni atoms, likely in the oxidized chemical state, can segregate to the NP surface and form adatom layers on the {111} facets of the octahedron.This conrms the ndings of Ahmadi et al., 20 who demonstrated preferential NiO x surface segregation by moderate thermal annealing (300 C).We believe that the observed elemental distribution at 300 C induced by the Pt and Ni interdiffusion within the octahedra is responsible for the elevated values of local compositional and structural disorder, i.e. the microstrain (Fig. 1c).
As mentioned above, at 400 C, the octahedral shape nally gave way to a cuboctahedral one, identied by clearly visible {111} and {100} facets (Fig. 3Q).This is induced by the migration of Pt atoms from the vertices to the {111} facets, resulting in a structure which appears at in the Z contrast and hence, a smooth, at Pt alloy surface.We observed similar transformations from octahedra to cuboctahedra during an in situ annealing TEM experiment. 10Based on the current data, we conclude that the morphological transformation from octahedra to cuboctahedra during heating is a thermodynamically driven effect rather than an effect of the gas atmosphere.This is also supported by the theoretical work of Wang et al., 21 showing that cuboctahedra are energetically favorable over octahedra due to complete {100} facet reconstruction.Furthermore, the morphological transformation to cuboctahedra and even more so the concomitant Pt and Ni intermixing are accompanied by a decrease of the lattice constant and microstrain as well as by a larger crystallite size of the PtNi domains (Fig. 1).
Finally, the octahedral shape was completely lost aer annealing at 500 C with only very few NPs remaining in the cuboctahedral shape (Fig. 3V1).These remaining cuboctahedra showed a more homogeneous distribution of the elements compared to all other samples.The former Pt-rich strip across the center of the cuboctahedral NPs is no longer visible in the elemental map (Fig. 3W1).Irregularly shaped NPs like those in Fig. 3V2, which potentially expose higher-index facets, are now found more frequently than cuboctahedral NPs.Furthermore, a homogeneous Pt and Ni distribution and a thin surface Ni layer characterize such NPs, as shown in exemplary EDX composition maps in Fig. 3W2-Y2.The observation of a more homogeneously alloyed particle structure in H 2 500 C is in full accordance with the trends in our XRD-derived structural descriptors such as low microstrain, contracted lattice parameters and the largest crystallite size.
The atomic-scale morphological changes offer a plausible explanation for the crystallite size-microstrain correlations: the strong decrease in local disorder in the PtNi-400 and PtNi-500 NPs (Fig. 1c) can be attributed to the evolution of octahedral particles into cuboctahedral particles with reduced concave surface curvature.The initial concave morphology, coupled with Pt and Ni interdiffusion and Ni segregation, is the source of local disorder and accounts for elevated values of microstrain in the particle ensemble.

Effect of local disorder and facet morphology on electrocatalytic ORR activity and stability
Catalytic ORR activity and particle facet morphology.To link the structure and facet morphology to catalytic ORR activity, all catalysts were tested in a three-compartment cell using the thin-lm rotating disk electrode (TF-RDE) technique.Prior to ORR testing, the nano-octahedra were electrochemically dealloyed, i.e. leaching of surface Ni atoms into the electrolyte, and, thereby, catalytically activated using electrochemical cycling in N 2 -saturated HClO 4 (0.1 M) in the potential range from +0.05 to +1 V RHE (100 mV s À1 ).The corresponding voltammograms (CVs) of cycle 25 are depicted in Fig. 4a.All samples displayed voltammetric features typical for Pt alloy facets: broad hydrogen ad-/desorption peaks (+0.06 to +0.4 V RHE ), double layer capacitive currents (+0.4 to +0.6 V RHE ), and Pt hydroxide and oxide peaks (+0.7 to +1 V RHE ).The electrochemically active surface area based on the hydrogen underpotential deposition charge (H upd ) from Fig. 4a remained stable up to 300 C (ECSA $40 m 2 g Pt À1 ) and dropped for the samples H 2 400 C and H 2 500 C (ECSA $30/25 m 2 g Pt À1 ).More detailed information about the ECSA data is given in Fig. S6 (ESI †).Since aer annealing only a slight increase in the particle size was detected by TEM (Fig. 2F), we conclude that the morphological transformations as well as the Pt diffusion occurring above 300 C (Fig. 2 and 3) must have inuenced the ECSA of the dealloyed particles, with Pt-concave octahedral NPs exhibiting a larger ECSA than well-alloyed cuboctahedral or spherical ones.This is plausible and can be rationalized as follows: aer performing the voltammetric activation/dealloying cycles, all segregated pure Ni surface atoms are assumed to be leached away, and the surfaces of the octahedral particles can be safely described to be signicantly Ni depleted.Accordingly, well-alloyed cuboctahedral PtNi particles retain a larger atomic ratio of Ni atoms near the surface aer activation/dealloying compared to the Ptconcave {111} octahedra having segregated at Ni {111} facets before activation.As hydrogen adsorption is energetically less favorable on Ni-rich alloy surfaces, 4,22 the resulting H upd charge is depressed for the samples H 2 400 C and H 2 500 C. In view of the experimentally observed facet morphology, we can conclude that the morphology of the activated/dealloyed catalyst particles follow the Pt-concave morphology of the annealed particles.In other words, the as-prepared, H 2 200 C and H 2 300 C samples exhibit concave Pt-rich {111} facets, while the H 2 400 C and H 2 500 C samples feature at Ni-richer {111} facets aer activation/dealloying (also see Fig. 6 for more details).The electrocatalytic Pt-based mass activity for the reduction of molecular oxygen to water was measured by anodic linear sweep voltammetry (LSV).Detailed experimental LSV curves are shown in Fig. S7 (ESI †).Fig. 4b shows a single maximum for H 2 300 C in the Pt-mass activity values at +0.9 V RHE of the PtNi nanoparticles as a function of their annealing temperature.The ORR activity sharply decreased with the onset of the morphological transformations of facets and particles from octahedral with Pt-concave {111} facets to cuboctahedral with nearly at facets to spherical with potentially higher-index facets.Taking into account the very similar particle size and the fact that cuboctahedra are conned by {111} and {100} facets, the lower activity of the catalyst H 2 400 C is in full agreement with earlier structure sensitivity studies that reported Pt 3 Ni {111} surfaces to be superior to Pt 3 Ni {100} surfaces. 4Anyway, we note that the catalyst H 2 400 C shows a similar activity as the as-prepared sample with Pt-concave {111} facets.Furthermore, our data conrmed that the complete loss of octahedral shape coupled to interdiffusion and surface alloying of Pt and Ni atoms (H 2 500 C) is very detrimental for the ORR activity.
Linking catalytic activity and local disorder.We compared the trends in the catalytic ORR activity of PtNi nano-octahedra with those of their structural parameters derived from diffraction analysis whose results are presented in Fig. 1b-d.In doing so, we uncovered a strong correlation between the catalytic activity and lattice microstrain.Fig. 4c illustrates the close relationship (green dashed line as a guide to the eye) between the experimental ORR activity and the degree of local lattice structural and lattice compositional disorder, the microstrain, of the PtNi nanoparticle ensembles.We prove once more that microstrain appears to be a suitable experimentally accessible predictor for catalytically ORR active Pt alloy nanomaterials as also reported earlier 23 at least within the present family of PtNi alloys.The activity-disorder trend is further conrmed by the similar values of the as-prepared sample and the catalyst H 2 400 C. The structural and morphological transformations and relaxations of H 2 400 C (see Fig. 1 and 2D) appear to nearly offset each other with respect to the resulting bulk lattice microstrain.Smooth, at Pt alloy {111} and {100} facets with a more homogeneous elemental Pt and Ni atom distribution in the cuboctahedral NPs of H 2 400 C (Fig. 2 and 3) yield a similar level of local disorder as the Pt-concave {111} facets in the octahedral NPs of the as-prepared catalyst.
The previous discussion of the catalytically most active structural state of the activated 300 C annealed PtNi nano-octahedra suggests an intrinsic link between the experimental facet morphology and the sample-averaged microstrain caused by chemical and lattice disorder.In fact, DFT-calculations of the binding energies of reaction intermediates of the ORR on Pt nanofacets with concave curvature have recently revealed that over-coordinated Pt atoms prevalent on surfaces with concave characteristics display lower thermodynamic limiting potentials. 24,25Invoking arguments from the Brønsted-Evans-Polanyi (BEP) relationships between thermodynamic driving forces and activation energies of elementary steps, smaller thermochemical overpotentials imply a lower kinetic barrier of the rate determining step, and, thus, improve catalytic ORR rates.We argue that, roughened by the Ni-depleting activation/dealloying step, the resulting concave particle facets display a large number of such catalytically active over-coordinated surface Pt atoms.At the same time, we argue that roughened concave particle facets with their inhomogeneous distribution of Pt and Ni display a level of lattice and compositional disorder, which exceeds that of well-alloyed at cuboctahedra or well-alloyed spherical particles.Hence, the former nanoparticles are more likely to exhibit large values of e 0 . 12orphological and performance stability.A major challenge related to the fuel cell operation of Pt-based bimetallic ORR cathode electrocatalysts is their performance stability during extended potential cycling, where both the composition and morphology affect their performance.Following the activity trends, the inuence of the annealing temperature on the catalyst performance stability was investigated during prolonged potential cycling.Two consecutive sets of 4000 cycles each were applied, and the ECSA and ORR activity values were recorded aer activation/dealloying, aer 4000 cycles and aer 8000 cycles.The corresponding CVs and LSVs are presented in Fig. S8 and S9 (ESI †), respectively.Fig. 5 shows the evolution of the Pt mass-based ORR activity of the annealed catalysts during the cycling test protocol.A monotonic decrease in activity was observed for the as-prepared catalyst as well as the catalysts H 2 200 C and H 2 300 C. The activity of all three samples converged despite major differences in their initial structural states.The activity degradation is attributed to leaching of Ni from the particle facets.In fact, continued electrochemical dissolution of Ni atoms from below the surface, even from initially Pt-enriched facets, is known to lower the ORR activity. 17The ECSA values of the three catalysts decreased as well (Fig. S10, ESI †), but not proportional to the Pt mass activity, indicating that surface modications alone cannot account for performance losses.Looking at the other two high temperature catalysts, it is evident that annealing of PtNi nano-octahedra to 400 C resulted in improved performance stability.Consistently, the ECSA of H 2 400 C remained very stable over 8000 cycles ($30 m 2 g À1 ).The initially low activity of H 2 500 C remained at a very low level over 8000 CVs.Imperfect {111} facets with Pt-concave curvature appear to be a recipe for high initial ORR activity, yet a reasonable balance between activity and stability is achieved by a morphological transformation from concave octahedral to a facet-healed cuboctahedral shape via thermal annealing.On comparing all catalysts together, it is found that the catalyst H 2 400 C maintained the highest Pt mass ORR activity aer 8000 cycles, and, as shown by STEM images (Fig. 3P and Q), it is characterized by cuboctahedral particles.This conclusion is in good agreement with a recent computational study by Mahata et al. 26 which proposed cuboctahedral Pt NCs to be electrochemically more stable than concave or convex octahedral Pt nanoparticles.
Morphological stability is a major challenge for shapecontrolled alloy nanocatalysts, as it directly controls the evolution of the surface area and intermediate adsorption via structure sensitivity effects, and, hence, plays a crucial role in the understanding of the empirical catalytic performance stability.This is why morphological changes of the PtNi nano-catalysts were investigated by TEM aer activation as well as aer 4000 and 8000 potential cycles during stability tests.TEM micrographs of the as-prepared, H 2 300 C and H 2 400 C nanoparticle catalysts are shown in Fig. 6.Additional images of H 2 200 C aer activation and of H 2 500 C aer activation and 8000 cycles are provided in Fig. S11 (ESI †).
Aer activation, the as-prepared catalyst (Fig. 6, le column) exhibited nano-octahedra with strongly concave {111} facets (Fig. 6A).Their particle surface morphology apparently converged to their initial Pt-based STEM morphology.We attribute this to its characteristic anisotropic elemental distribution (Fig. 3B and D): Ni atoms were leached from the at Ni segregated {111} facets and, thus, gave way to the observed excavated concave facets with a Pt-enriched surface.Aer $4000 potential cycles, octahedra with further excavated facets, and hexapod-shaped NPs emerged, due to prolonged Ni leaching from the surfaces.In fact, compositional analysis conrmed that the Pt : Ni ratio increased from 40 : 60 before electrochemical cycling to 93 : 7 (EDX) aer cycling.Thus, only 14 at% Ni were le aer 4000 cycles and 7 at% aer 8000 cycles, and this explains the severe loss in ORR activity.A similar mechanism was observed for the catalysts H 2 200 C (Fig. S11A, ESI †) and H 2 300 C (Fig. 6, middle column): initial dealloying and Ni dissolution resulted in concave and excavated octahedral NPs.A signicantly distinct behavior, however, was noted for H 2 300 C aer 4000 cycles, where neither excavated octahedral NPs or any form of hexapod-shaped NPs were le behind.The particles were either rounded or were attached by their facets to form particle agglomerated clusters.The degradation continued aer 8000 cycles and resulted in irregularly shaped clusters.
A distinct degradation behavior was displayed by the catalyst H 2 400 C (Fig. 6, right column).This material preserved its alloyed cuboctahedral particle shape aer activation.Surprisingly, cuboctahedra were partially present even aer 8000 cycles.Partial cluster formation by facet attachment of neighboring particles was prevalent, as well.In fact, the shape stability of the NPs of H 2 400 C is accompanied by a low degree of Ni dissolution as determined by EDX of several catalyst agglomerates.41 at% Ni are le aer 4000 cycles and 37 at% Ni aer 8000 cycles, whereas H 2 300 C contains only 19 at% Ni aer 4000 and 8000 cycles.See detailed compositional stability data aer electrochemical cycling in Table S3 (ESI †).In the NPs of H 2 500 C, no signicant morphological changes were observed aer electrochemical cycling (Fig. S11B and C, ESI †).
These morphological observations can plausibly account for the experimental performance stability trajectories.The activated concave octahedral particles of H 2 300 C with their enhanced local disorder (microstrain) showed the highest initial ORR activity, and the activated cuboctahedral NPs with at {111} and {100} facets or spherical ones showed lower initial ORR activity.As the NPs continued to get depleted near the surface due to the prolonged electrochemical cycling and once they started to lose their concave octahedral shape by transforming into Pt-rich hexapods (Fig. 6D and G) or aggregated clusters (Fig. 6E and H), their initial high ORR activity dropped.On the other hand, the well-alloyed cuboctahedral particles annealed at 400 C were able to retain their Ni content to a larger degree and appeared morphologically more resistant to potential cycling (Fig. 6F and I), showing only little change in the shape as well as ORR activity aer 8000 cycles.

Conclusions
We set out to explore whether PtNi nano-octahedra with rather ordered, smooth alloy facets, or nano-octahedra with rather imperfect, disordered, concave facets are more active and stable ORR electrocatalysts, and which structural parameter controls and possibly predicts their activity.To check this, we have investigated the relationship between some bulk structural parameters, the individual particle morphology and the catalytic ORR activity of a family of annealed octahedral-shaped PtNi nanoparticles.
We found that the post-synthetic annealing procedures between 200 and 500 C transformed the as-prepared nanooctahedra stepwise into faceted cuboctahedra and nally into rather spherical nanoparticles with a mix of potentially higherindex facets.We have identied the experimentally accessible sample-averaged microstrain, a measure of local disorder in crystalline phases, as the best predictor and descriptor for the electrochemical ORR activity of such nano-octahedra.
Nano-octahedra with high microstrain and concave Pt curvature catalytically outperformed cuboctahedra with at, well-alloyed {111} and {100} nanofacets.More specically, concave nano-octahedra with enhanced local compositional and structural disorder (microstrain) were invariably superior to more ordered and well-alloyed PtNi nanoparticles.Accordingly, our results describe a new structural feature benecial for ORR activity deviating from the conventional concept of well-ordered and well-alloyed Pt 3 Ni(111) skin surface as the mechanistic origin for enhanced experimental ORR activities in nanooctahedra.
While catalytically active, the concave PtNi octahedra lacked sufficient morphological stability, lost excessive amount of Ni and transformed into Ni poor hexapods, which is why cuboctahedral shaped PtNi nanoparticles prepared at 400 C ultimately offered the most favorable balance between ORR activity, performance stability, and morphological stability.Accordingly, such nanoparticles are proposed as promising future PEM cathode fuel cell catalysts.

Fig. 1 X
Fig. 1 X-ray diffraction study of the as-prepared and annealed samples: (a) measured XRD patterns, where red and yellow bars indicate pure metals Pt fcc (ICSD 4-0802) and Ni fcc (ICSD 4-0850).Dashed lines are a guide to the eye for the peak shift to higher angles with increasing temperature.(b-d) Structural impact of annealing temperature as derived from Rietveld refinement: (b) lattice constant, (c) microstrain and (d) crystallite size.Dashed lines are a guide to the eye.

Fig. 2
Fig.2 (A-E) Evolution of the morphology upon annealing in hydrogen: TEM micrographs (BF) of various PtNi nanoparticles of the as-prepared sample and samples annealed at different temperatures; (F) particle sizes with a dependence on annealing temperatureerror bars represent the calculated error of each particle size (details of the calculation given in ESI, † page 6).

Fig. 3
Fig. 3 HAADF STEM images (Z contrast) and EDX elemental maps of shaped PtNi nanoparticles without (A-E) and after annealing in hydrogen at different temperatures (F-T) -(F-J) 200 C, (K-O) 300 C, (P-T) 400 C and (U-Y) 500 C: (A, F, K, P and U) low magnification overview HAADF STEM images of the nanoparticle ensembles; (B, G, L, Q and V) high resolution HAADF STEM images of shaped PtNi nanoparticles oriented close to a h110i zone axis; (C-E, H-J, M-O, R-T, and W-Y) EDX elemental maps of the corresponding nanoparticles; Pt and Ni are colored in red and green, respectively.

Fig. 4
Fig. 4 Correlation of the structure and catalytic ORR activity for shaped PtNi nanoparticles: (a) cyclic voltammograms of the 25th cycle of activation in a N 2 -saturated electrolyte in the potential range from +0.05 to +1 V RHE with 100 mV s À1 .(b) Pt mass-based ORR activity, J m , evaluated at +0.9 V RHE during an anodic voltammetric scan in an O 2 -saturated electrolyte in the potential range from +0.05 to +1 V RHE with 5 mV s À1 at 1600 rpm.The potentials are IR corrected, and 0.1 M HClO 4 was used as the electrolyte.(c) Correlation of microstrain and ORR activity.Sample names are indicated at each data point; the green dashed line represents the proposed trend and acts as a guide to the eye.

Fig. 5
Fig.5Performance stability of shaped PtNi nano-catalysts as a function of their annealing temperature: Pt mass activity, J m , for the electrochemical ORR after 4000 (green) and 8000 (brown) potential cycles.The "activated" value (purple) is the ORR activity after 25 activation cycles (+0.05 to +1.0 V RHE , 100 mV s À1 ) in N 2 .Conditions: oxygen transport-corrected kinetic J m values were evaluated at +0.9 V RHE in an O 2 -saturated electrolyte with anodic scans in the potential range from +0.05 to +1 V RHE with 5 mV s À1 at 1600 rpm.Stability cycling was performed in a N 2 -saturated electrolyte in the potential range from +0.5 to +1.0 V RHE (50 mV s À1 ).The potentials are IR corrected, and 0.1 M HClO 4 was used as the electrolyte.

Fig. 6
Fig. 6 Morphological stability of shaped PtNi nanoparticles: TEM micrographs of samples without and with annealing after electrochemical cycling: (A-C) after activation (25 CVs), (D-F) after 4000 cycles, and (G-I) after 8000 cycles.(A, D and G) the as-prepared PtNi octahedra, (B, E and H) H 2 300 C catalyst sample, (C, F and I) H 2 400 C catalyst sample.