# Synthesis of highly dispersed Pt nanoparticles into carbon supports by fluidized bed reactor atomic layer deposition to boost PEMFC performance

### Abstract

The performance of proton exchange membrane fuel cells (PEMFCs) depends on the controlled size, dispersion and density of Pt nanoparticles (NPs) on carbon supports, which are strongly affected by the carbon characteristics and fabrication methods. Here, we demonstrated a high-performance Pt/carbon catalyst for PEMFCs using fluidized bed reactor atomic layer deposition (FBR-ALD) that was realized by an effective matching of the carbon supports for the FBR-ALD process and an optimization of the ionomer content during the preparation of the membrane electrode assembly (MEA). For this, the synthesis of Pt NPs was conducted on two porous supports (Vulcan XC-72R and functionalized carbon) by FBR-ALD. The functionalized carbon possessed a higher surface area with a large pore volume, abundant defects in a disordered structure and a large number of oxygen functional groups compared to those of the well-known Vulcan carbon. The favorable surface characteristics of the functionalized carbon for nucleation produced Pt particles with an increased uniformity and density and a narrow size range, which led to a higher electrochemical surface area (ECSA) than that of Pt/Vulcan carbon and commercial Pt/carbon. The PEMFC test of the respective Pt/carbon samples was investigated, and highly dense and uniform Pt/functionalized-carbon showed the highest performance through optimization of the higher ionomer content compared to that for the ALD Pt growth on Vulcan carbon and commercial Pt/carbon. In addition, the Pt catalyst using ALD demonstrated a significant long-term stability for the PEMFC. This finding demonstrates the remarkable advantages of FBR-ALD for the fabrication of Pt/carbon and the ability of functionalized carbon supports to achieve a high PEMFC efficiency and an enhanced durability.

## Introduction

To mitigate the use of fossil fuel-derived energy for transportation, proton exchange membrane fuel cells (PEMFCs) are one of the most promising and attractive power sources1,2,3. Pt is an outstanding active material for catalysts in PEMFC stacks, but its successful commercialization is lagging due to its high cost4. To make the technology economically viable, a reduction in the Pt loading5 and an increase in the efficient Pt surface area should be established simultaneously to obtain an excellent PEMFC activity and stability6,7,8. In addition, an improvement in the fuel cell efficiency has been associated with the optimized three-phase interface that is composed of an ion-conducting electrolyte (ionomer) next to a solid catalyst surface9,10,11,12. After reacting H2 gas molecules in the solid phase of the anode, the protons meet in the electrolyte phase and then react with O2 in the solid-electrolyte interface, producing water as a by-product13. To enhance the efficiency of the three-phase interface, protons in the three-dimensional network of the fuel cell should be easily accessible to every portion of the cell by optimizing the ionomer content.

For PEMFCs, a Pt catalyst (Pt/carbon black) provides a large surface area and large accessible pores for hydrogen and oxygen molecules to contact the Pt surface14,15. However, it is not easy to uniformly deposit Pt nanoparticles (NPs) in porous carbon supports because the textural properties (surface area, porosity, and pore volume), structural defects and functional groups on the carbon surface strongly affect the growth mechanism during Pt deposition13,16. These characteristics of the carbon can act as strong binding sites to anchor the Pt NPs17. Porous carbon with an internal porosity can offer a high surface area for a large number of Pt NPs compared to solid carbons, e.g., acetylene black and graphitized carbons18. The defect structures of the carbon can play an important role in controlling the Pt deposition density due to their enhanced chemical reactivity compared to that of an inert carbon lattice17,19. In addition, during the deposition process, a large number of functional groups on the carbon surface can promote the nucleation of Pt NPs and hinder NP agglomeration, resulting in a reduction in the Pt NP size and a narrow size dispersion, which can improve the degradation characteristics20,21,22. Therefore, it is demonstrated that a carbon support with favorable textural properties, optimized structural surface defects and oxygen functional groups should be considered for Pt NP deposition to fabricate efficient Pt/carbon catalysts for PEMFCs.

To synthesize Pt/carbon, several wet-chemical23,24, and gas-phase processes25,26 have been extensively studied. However, most of the processes involve complicated steps and produce a wide range of Pt NP size distributions with high Pt loading and low productivity rates, which demonstrate poor long-term durability. Compared to these methods27,28, atomic layer deposition (ALD) can have many unique inherent merits for preparing Pt NPs on porous carbon supports. It allows the vapors of the precursor to penetrate into deep regions of the porous carbon support for uniform deposition of Pt NPs, which can lead to precise control of the size of the NPs within the porous matrix to improve the electrochemical surface area (ECSA) with a low Pt loading29,30,31. To date, most of the studies using ALD have focused on thin film-based depositions, such as carbon paper, carbon on glassy carbon and carbon cloth29,31,32,33. To fabricate powder coatings on a large scale, several modified ALD systems, such as static and rotary reactor methods, have been studied, and have synthesized diverse NP materials on porous materials34,35,36. Among them, to synthesize the Pt/carbon catalyst for commercialization of PEMFCs, a fluidized bed reactor (FBR) ALD is an excellent modified ALD system due to its excellent gas transfer, uniform NPs and large production quantity37,38. However, in light of a few reported FBR-ALD studies21,38, the synthesis of a FBR Pt catalyst through a process with increased efficiency and speed, and an improved fluidizing behavior is highly desired. In addition, the growth behavior of the ALD process also strongly depends on the surface conditions39,40,41, which can affect the uniformity, particle size and density of the Pt NPs toward improving the electrochemical surface active area (ECSA) and durability. However, the effect of the carbon support on Pt formation based on wet processing has been intensely studied despite the different growth mechanisms between the wet process and ALD14,19. Therefore, it is crucial for the ALD process to produce these favorable characteristics of carbon black to control the size, density and distribution of uniform Pt NPs to improve the PEMFC activity, reduce the Pt loading, and commercialize the production of FBR-ALD Pt/carbon catalysts.

Herein, therefore, we report a very efficient, fast and scalable FBR-ALD process for a highly uniform Pt catalyst on two well-known porous carbons, Vulcan and Vinatech. The effect of the carbon supports on tuning the deposited Pt NP size and density was systematically investigated. The textural properties (surface area, mesoporosity and pore volume), oxygen functional groups and structural defects of the carbon supports can influence the Pt NP deposition characteristics, uniformity and density of the NPs in the ALD process. Based on a comprehensive study of FBR-Pt/carbon catalysts, electrochemical properties and a test of the fuel cell activity were implemented, and uniformly dispersed and highly dense Pt NPs produced using FBR-ALD with an optimized ionomer content showed efficient fuel cell performance with excellent stability.

## Materials and methods

### Fabrication of the Pt catalyst using the FBR-ALD process

The synthesis of Pt particles on carbon supports was achieved by using an FBR-ALD system. The two carbon supports, Vulcan XC-72 R and functionalized carbon (VFC-SP0450), are referred to as Vulcan and Vinatech, respectively. After citric acid treatment, a controlled cluster size (60–120 µm) of the carbons (0.4 g) was inserted in the chamber to thoroughly fluidize them (see supporting information for a more detailed synthesis process of the Pt catalyst). The base and working pressures were kept at 0.01 Torr and 0.4 Torr, respectively. The reactor was heated to 300 °C, and a gas line was maintained at 100 °C. The Pt precursor and reactant were MeCpPtMe3 (trimethyl (methyl cyclopentadienyl) platinum (IV), i-Chem Co.) at 30 °C and UHP (ultra-high purity) O2 gas, respectively. Before the first cycle, the preprocessing was performed with Ar gas at 50 sccm (30 s) and then at 100 sccm (60 s) to prevent abrupt fluidizing of the powder. During the process, UHP Ar gas at 100 sccm was continuously supplied into the reactor for constant MeCpPtMe3 precursor bubbling, purging and fluidizing of the powder. One cycle consisted of a MeCpPtMe3 pulse (120 s), purge (90 s), O2 pulse with 30 sccm (90 s) and then another purge (90 s). For the two carbons, 15 cycles (approximately 30 wt%) were processed to compare the Pt NP density and size distribution, and these were analyzed to achieve an increased fuel cell performance. Commercial Pt/C (Premetek, 30 wt%) was used as a comparison with the ALD catalysts.

### Characterization of the Pt catalysts

The surface area and porous structure were investigated by using Brunauer-Emmett-Teller analysis (BET, Micromeritics, ASAP 2010 analyzer). The chemical bonding was identified using X-ray photoelectron spectroscopy (XPS, Thermo Electron Corporation, MICROLAB 350). Fourier transform infrared spectroscopy (FTIR, Bruker, Vertex 80 v) spectra were used to analyze the carbon bonding type, which were obtained from 4000 to 400 cm−1 (4 cm−1 resolution) with a Vertex 80 v. Raman spectra (Nano Base, XperRamII) were obtained using a 532 nm laser with a power of 3.0 mW at room temperature. The crystallinity and crystalline size were investigated by X-ray diffraction (XRD, Bruker, D8 ADVANCE) using Cu-Kα1 radiation with a wavelength of 1.5418 Å. Field-emission transmission electron microscopy (FE-TEM, FEI, TALOS F200X) operating at 200 kV was used to analyze the visible particle size, particle dispersion and density. The particle size and density of the STEM images were calculated by Image-Pro Plus processing and analysis software. To identify the electrochemical activity, cyclic voltammetry (CV, Autolab, PGSTAT302N) and oxygen reduction reaction (ORR) tests were implemented by using the three-electrode method. This method consisted of a glassy carbon electrode 5 mm in diameter as the working electrode, Ag/AgCl as the reference electrode and Pt foil as the counter electrode. The potential was given versus the reversible hydrogen electrode (RHE), and 0.1 M HClO4 was used as the electrolyte. The glassy carbon electrode was polished with a 1 μm Al2O3 powder and washed with DI water before the experiments. To add the Pt catalyst onto the glassy carbon, isopropanol (5 mL) and Nafion® solution (0.2 mL of 5 wt% solution) were first mixed in DI water (39.8 mL). Then, this solution and 5 mg of the Pt catalyst were added to a vial container. To make the ink, this mixture was sonicated in the vial. Then, 15 μL of the ink was deposited onto the working electrode (25 μgPt/cm2) and dried in a thermal oven at 80 °C. The CV was measured at a sweep rate of 20 mV/s in the saturated Ar electrolyte. Linear scan voltammetry for the ORR activity measurement was performed using a rotating disk electrode (RDE) system with a rotation speed of 1600 rpm in an O2-saturated electrolyte at a 20 mV/s scan rate.

### MEA preparation

The membrane electrode assembly (MEA) was prepared from the Pt catalyst made by ALD for both the cathode and anode as a function of Nafion® solution content. The Nafion® percentage was calculated using the following equation:

$${\mathrm{Nafion}}\textregistered \;{\mathrm{loading}} = \frac{{{\mathrm{Nafion}}\left( {\frac{{{\mathrm{mg}}}}{{{\mathrm{cm}}^2}}} \right)}}{{{\mathrm{Nafion}}\left( {\frac{{{\mathrm{mg}}}}{{{\mathrm{cm}}^2}}} \right) + {\mathrm{catalyst}}\left( {\frac{{{\mathrm{mg}}}}{{{\mathrm{cm}}^2}}} \right)}} \times 100$$

The catalyst ink was made by adding Nafion® solution with 2-propanol to the Pt catalyst powder. The resulting ink was sprayed directly onto one side of the pretreated dried membrane (Nafion 212) and dried by heating under vacuum at 70 °C for 30 min. The reverse side of the membrane was also subjected to a similar process to obtain the anode and cathode catalyst layers on the membrane. The catalyst loading was adjusted to 0.1 mg/cm2 on the anode and 0.4 mg/cm2 on the cathode. Both electrodes had an active surface area of 5 cm2. The MEAs were sandwiched between two gas diffusion layers (GDLs, N1S 1007, Ce Tech) and then installed in graphite plates with a serpentine flow field. All cells were operated with a relative humidity of 100% and with H2 and O2 at a cell temperature of 70 °C. To evaluate the durability of the catalysts in single cells, triangle voltage cycling tests were carried out between 0.6 and 1.0 V at a sweep rate of 50 mV/s. The anode side was fed with hydrogen (40 sccm) and served as the reference and counter electrodes. The cathode side was fed nitrogen (100 sccm) and served as the working electrode. After 3k, 10k, and 30k cycles, the polarization curves were measured. Electrochemical impedance spectroscopy (EIS) was measured with a 20 A current booster (PGSTAT30) and performed at a DC potential of 0.9 V with an AC frequency range from 10k Hz–0.01 Hz and AC amplitude of 5 mV before and after the durability test.

## Results

### Carbon surface characteristics

Pt catalysts were synthesized on the fluidizing carbon supports by FBR-ALD with 15 cycles that consisted of a MeCpPtMe3 pulse, a purge, an O2 pulse and another purge, as shown in Fig. 1a. During Pt NP deposition, the textural properties (surface area, porosity, and pore volume), structural defects, and functional groups of the carbon supports can play a key role by providing abundant binding sites for anchoring the Pt NPs, enabling control of the particle density and size distribution19. Before deposition, pretreatment of the carbons was conducted in a citric acid solution to maximize the functional groups for Pt nucleation (see experimental section for details in the supporting information). The multipoint BET nitrogen adsorption–desorption isotherms for the two different carbon supports (Vulcan and Vinatech carbons) before and after deposition were obtained to systemically reveal the effect of the textural properties on the growth mechanism of the Pt NPs produced by FBR-ALD. The isotherms of all the samples showed type IV characteristics with an H3 hysteresis loop42 (Fig. 1b), which was attributed to the presence of slit-like mesopores. The pore size distribution curves (Fig. 1c) showed that both samples exhibited mesopores and macropores13. A sharp and broader peak below 10 nm was attributed to the presence of a large number of mesopores in the Vinatech carbon, whereas a low intensity distribution curve for mesopores was found for the Vulcan carbon. After synthesizing the Pt/carbon (approximately 30 wt%) support (Fig. S1), the peak intensities of the pore size distributions decreased for both carbons, suggesting Pt loading on the carbon support and subsequent pore filing43. The BET specific surface area and pore volume of the bare and Pt-deposited Vulcan and Vinatech carbons are summarized in Table 1 and illustrated in Fig. 1d. The Vinatech carbon possessed a specific surface area (370.92 m2/g) and pore volume (0.9839 cm3/g) that was ~2.5 and ~1.6 times larger than those of the Vulcan carbon (145.45 m2/g and 0.6135 cm3/g, respectively). It was noted that the decrease in surface area of the modified Vulcan carbon (after chemical treatment) compared to that of reported Vulcan carbon44 could be due to blockages at the entrances of the carbon pores by the resulting functional groups (Fig. S2)45,46. After Pt deposition on both carbons, the specific surface area and pore volume of both Pt/carbons were found to decrease compared to those of the bare carbons. However, the Pt/Vinatech still exhibited a higher surface area and pore volume than the deposited Pt/Vulcan and even bare Vulcan carbon. It is worth mentioning that after Pt deposition, mesopores below 10 nm in the Vinatech carbon still existed in the sample, which would help the efficient transport of gas molecules and protons and enable transport of the molecules from the Pt surface.

ALD Pt deposition on a carbon support is greatly influenced by the oxygen-containing functional groups on the carbons25. To identify the state of the oxygen functional groups on the carbon supports, FTIR vibrational spectroscopy was carried out. The FTIR spectra of the Vinatech and Vulcan carbon supports are shown in Fig. 2a. The oxygen groups of vibrational bands at ~1160 cm−1 47, ~1400 cm−1, 1600–1700 cm−1 48,49, and 3400 cm−1 correspond to the C–O (stretching vibration), O–H (stretching), OH (bending vibration) overlapped with C=C (stretching vibration) and C=O (stretching) groups, and O–H (stretching vibrations) in adsorbed water, respectively. It is noted that the peak corresponding to the C–O vibration was not found in the Vulcan carbon. It is also worth mentioning that the Vinatech had more oxygen functional groups than Vulcan and therefore provided more binding nucleation sites for high-density Pt deposition. However, it is very difficult to distinguish the peaks of the other functional groups because of overlapping and similar peaks for both carbons. Therefore, to further clarify the oxygen functional group content of both carbons, XPS analysis was performed, as shown in Fig. 2(b, c). The C 1s spectra of both carbons were deconvoluted into four components located at 284.6 eV, 284.9 eV, 286.5 eV, and 288.5 eV corresponding to the C–C (sp2), C=C (sp3), hydroxyl C–O, and carbonyl C=O groups50, respectively. The relative contributions of each bond are listed in Table 2. Compared to the Vulcan carbon (Fig. 2c), the Vinatech exhibited a lower peak intensity from C–C bonding and a wider oxidized carbon peak (Fig. 2b). The percentage of oxygen functional groups (C–O and C=O) in the Vinatech carbon was higher than that in Vulcan carbon (Fig. 2d). These oxidized functional groups are the key factor to growing ALD Pt particles on the carbon supports. Figure 3e shows that the Pt growth step by ALD can be formulated as follows29.

### Precursor pulse step

$${\mathrm{Carbon}}\;{\mathrm{support}}\; - {\mathrm{O}}^\ast \;\left( {{\mathrm{ads}}} \right)\; + {\mathrm{MeCpPtMe}}_{\mathrm{3}}\left( {\mathrm{g}} \right)$$
$${\mathrm{Carbon}}\;{\mathrm{support}}-{\mathrm{MeCpPtMe}}_{\mathrm{2}}^\ast \;\left( {{\mathrm{ads}}} \right)\; + \;{\mathrm{CO}}_{\mathrm{2}}\left( {\mathrm{g}} \right)\; + {\mathrm{H}}_{\mathrm{2}}{\mathrm{O}}\;\left( {\mathrm{g}} \right) + {\mathrm{other}}\;{\mathrm{products}}$$

### O2 pulse step

$${\mathrm{Carbon}}\;{\mathrm{support}}\; - {\mathrm{MeCpPtMe}}_{\mathrm{2}}^\ast \;\left( {{\mathrm{ads}}} \right)\; + \;{\mathrm{O}}_{\mathrm{2}}\left( {\mathrm{g}} \right)$$
$${\mathrm{Carbon}}\;{\mathrm{support}} - {\mathrm{Pt - O}}^\ast \;\left( {{\mathrm{ads}}} \right)\; + \;{\mathrm{CO}}_{\mathrm{2}} + \;{\mathrm{H}}_{\mathrm{2}}{\mathrm{O}}\;\left( {\mathrm{g}} \right)\; + \;{\mathrm{other}}\;{\mathrm{products}}$$

where “*” represents active surface species and “Carbon support -O*” means chemisorbed oxygen on the carbon support. Based on this ALD growth mechanism, many functional groups on the surface of the carbon can be expected to provide many nucleation sites for the Pt deposition.

Raman spectroscopy is an important tool to reveal the structural defects and ordered/disordered structure of a carbon-based material. Raman spectra (Fig. 3a) of both carbons show the presence of two bands positioned at 1340 and 1580 cm−1, corresponding to the D and G bands, respectively. The G band is related to the E2g vibration mode of sp2 carbon domains and can be used to determine the degree of graphitization51. The D band is derived from the structural defects and disordered structures of sp2 carbon. The band intensity ratio of the Vinatech carbon support was observed to be ID/IG = 3.54, which is higher than that of the Vulcan carbon support (ID/IG = 1.55). This means that the Vinatech had more structural defects (Fig. 3b) and a larger amount of disordered carbon (Fig. 3c), which can also provide more anchoring points for Pt deposition (Fig. 3b inset). However, after Pt loading on both carbons, the intensity ratio (ID/IG) of the Pt/Vinatech and Pt/Vulcan was found to decrease to 1.55 and 1.23, respectively. It is noted that the degree of ID/IG reduction in the Vinatech after depositing Pt NPs was 58%, whereas the degree of ID/IG reduction was 21% for the Vulcan. This indicated that after deposition, structural defects and the disordered structure of the Vinatech support were consumed as nucleation sites and arranged in an ordered structure, which can suggest a high-density Pt NP deposition on Vinatech. The XRD spectra of the bare and Pt-deposited Vulcan and Vinatech carbon supports are shown in Fig. 3d. Two peaks appearing near 25° and 43°, which correspond to the (002) and (100) planes of carbon, respectively, were observed in both carbons. The (002) diffraction peak was related to the disordered carbonaceous interlayer52,53, and the (100) diffraction peak was attributed to crystalline carbon54. High intensities of the (100) peak relative to that of the (002) peak can indicate an improved degree of graphitization. The I(100)/I(002) intensity ratios of the Vinatech and Vulcan carbon supports were calculated to be 0.159 and 0.204, respectively. This demonstrates that the Vinatech had more structural defects than the Vulcan, which is supported by the Raman spectra (Fig. 3a). Deposited Pt NPs on both carbons show the (111), (200), and (220) orientations with a Pt FCC (face-centered cubic) structure28. The grain size of 2.66 nm for the Pt/Vinatech was calculated using Scherrer’s equation, and the grain size for the Pt/Vulcan was found to be 3.42 nm. Considering the same Pt loading at approximately 30 wt%, the Pt/Vinatech had a denser and smaller Pt NP distribution on the carbon matrix.

### Pt deposition formations on the carbons

Based on the above results, it is clear that the Pt deposition on the carbon supports (Vinatech and Vulcan) by FBR-ALD were affected by the surface area, pore size, and oxygen functional groups on the carbon surface, as well as the presence of many structural defects and disordered carbon structures. To visibly inspect the Pt deposition behavior on the carbon supports, bright-field (BF) TEM images and high-angle annular dark-field (HAADF) TEM images were obtained. The images of the Pt/Vinatech, Pt/Vulcan, and commercial Pt/carbon (Premetek 30 wt%) are illustrated in Fig. 4. The Pt/Vinatech sample had a very uniform Pt distribution throughout the low-magnification BF- and HADDF-TEM images (Fig. 4a). The Pt/Vulcan carbon (Fig. 4b) also appeared uniform but the uniformity was less than that of the Pt/Vinatech, while the commercial Pt/carbon (Premetek, 30 wt%) had a wide Pt NP distribution range that was somewhat uniform but contained mostly nonuniform agglomerated NPs (Fig. 4c). The high-magnification TEM images measured from two parts in the low-magnification image (Fig. 4a) show a uniform and high-density Pt dispersion, indicating a wide uniformity range, which was even identified at low cycles (Fig. S3). Both the BF-TEM and HAADF images show that more uniformly distributed and denser Pt NPs formed in the Pt/Vinatech sample than in Pt/Vulcan and commercial Pt/carbon samples. In addition, the HAADF image of the Pt/Vinatech exhibited a denser amount of more visible Pt NPs compared to those in the BF-TEM image. This means that Vinatech possessed a highly porous structure inside, in which many Pt NPs were deposited. In addition, this result demonstrated that the favorable textural properties and abundant structural defects, disorder and functional groups on the Vinatech carbon during the ALD process provided a larger number of active sites that anchored many Pt NPs inside the carbon surface compared to those of the other carbons16.

To summarize the Pt distribution and density, numerical figures for the particle size, distribution and density are shown in Fig. 5. To provide relatable values, they were calculated and averaged from the respective HAADF images in Fig. 4 and S4. Narrow and small Pt particle size (1.5–2.5 nm) distributions on the Vinatech (Fig. 5a) were observed, while Pt/Vulcan exhibited a 2–3 nm particle size with a small width distribution (Fig. 5b). The commercial Pt/carbon was found to have a larger Pt particle size of 1.5–3 nm with a wider particle dispersion than those for the Pt/Vinatech or Pt/Vulcan. Based on this, ALD provided a uniform Pt particle deposition on the carbon supports (Vinatech and Vulcan) compared to that on the commercial Pt/carbon catalyst (Fig. 5c) synthesized by the wet process. However, the Vinatech was a better supporting material for uniform Pt deposition than the Vulcan. As seen in the TEM image (Fig. 4a), the Pt/Vinatech exhibited a Pt particle density that was approximately 1.6 times denser than that on the Pt/Vulcan (Fig. 5d). Although the Pt loading was similar, the Vinatech provided more uniform and smaller Pt NPs; ultimately, the Vinatech produced a denser Pt NP distribution than the Pt/Vulcan. Compared to those for the Pt/Vulcan, the commercial Pt/carbon exhibited a lower density with a wide range of particle densities.

### Electrochemical performance of the Pt catalysts

To demonstrate the Pt catalyst activity by FBR-ALD, the CV curves of Pt/Vinatech, Pt/Vulcan and commercial Pt/carbon catalyst in 0.1 M HClO4 with a 20 mV/s sweep are illustrated in Fig. 6a. The peaks consist of three parts: the hydrogen adsorption-desorption region (from 0.05 to 0.3 V), the double layer region (from 0.3 to 0.7 V) and the surface Pt oxidation region (from 0.7 to 1.2 V)55. From the hydrogen desorption region, the ECSA can be determined and calculated from the following equation56:

$${\mathrm{ECSA}} = \frac{{{\mathrm{Q}}_{\mathrm{H}}}}{{\left[ {{\mathrm{Pt}}} \right] \times 0.21}}$$

where “QH” represents the charge for hydrogen desorption (mC/cm2), “[Pt]” is the Pt loading on the glassy carbon electrode (mg/cm2), and the number “0.21” represents the charge required to oxidize the adsorption of the H2 monolayer on the Pt surface. The ECSAs of the Pt/Vinatech, Pt/Vulcan and commercial Pt/carbon catalysts were found to be 90.8, 78.9, and 72.6 m2/g, respectively. Considering the same amount of Pt loading in the respective samples, the Pt NPs in the Pt/Vulcan and commercial Pt/carbon possessed a low active surface area owing to the larger particle size with a low density, while the high Pt dispersion with a fine particle size in the Vinatech (illustrated in Fig. 6b) provided a large number of accessible active surface areas for catalytic reaction. However, a higher ECSA was obtained for the Pt/Vulcan than that for the commercial Pt catalyst with its partially agglomerated and nonuniform Pt distribution, as seen from the TEM image (Fig. 4c). Figure 6c displays the ORR polarization curves measured in an O2-saturated 0.1 M HClO4 solution using the RDE at 1600 rpm. The Pt/Vintech showed a higher ORR activity than the Pt/Vulcan. This can be due to the efficient charge transfer of uniformly dispersed and dense Pt NPs in the Pt/Vinatech. However, the ORR activity of the Pt/Vulcan was even higher than that of the commercial Pt catalyst.

### Performance and durability of the PEMFC cells

The relative particle density and distribution can influence the optimization of ionomer content, as well as the performance of the MEA tests. Polarization curves from the PEMFC with ALD Pt/both-carbons and commercial Pt/carbon catalyst are shown in Fig. 7 as a function of Nafion® content. In addition, power density curves were also obtained (Fig. S5). The electrode performance of the Pt/Vinatech was found to increase with increasing Nafion® content from 25 to 35 wt%, which had the maximum electrode performance, and then it eventually decreased until a Nafion® content of 45 wt% was reached (Fig. 7a). Many studies have been reported to reveal PEMFC characteristics with different ionomer contents57,58,59. As illustrated in Fig. 7d, at a low ionomer content, a poor electrode performance was observed from the high cell impedance, which was due to the discontinuous proton-conducting ionomer networks, few three-phase interfaces and poor contact between the electrolyte with the catalyst60. On the other hand, a high ionomer content caused the blocking of the catalyst sites from the gas molecules, resulting in a lowered gas permeability and an increase in the mass transport distance59. The Pt/Vulcan showed the efficient cell performance of Nafion® at 25 wt%, indicating that a lower Nafion® content was needed for the optimization than that needed for the Vinatech (Fig. 7b). A similar and optimized 25 wt% Nafion® content for the commercial Pt/carbon catalyst was obtained by controlling the Nafion® from 20 to 30 wt% (Fig. 7c). These results can be explained by the Pt catalyst surface areas, as shown in Fig. 1 and Table 1. According to previous reports61, the ionomer content is highly dependent on the catalyst surface area. All Pt catalyst surfaces should be wrapped by the Nafion® ionomer for efficient three-phase interfaces, and then the ionomer can maintain its network with the catalyst9. Therefore, the content of ionomers would be high for a Pt catalyst with a large surface area, resulting in a considerable Nafion® content being needed for the Pt/Vinatech with the highest BET surface area herein, while both the Pt/Vulcan and commercial Pt/carbon catalyst were optimized with a lower amount of 25 wt% Nafion®, probably due to the comparable surface area. At the optimized Nafion® content, the current density at 0.6 V was found to be 1.55, 1.46, and 1.42 A/cm2 for the Pt/Vinatech, Pt/Vulcan and commercial Pt/carbon, respectively (Table 3). This result can be explained by the Pt active surface area. The Pt/Vinatech shows the best performance with the highest mass activity (Fig. S6) in the MEA test due to its high ECSA62.

The durability of Pt catalysts under the operating conditions of fuel cells can be influenced by the size, uniform dispersion and density of Pt NPs. To investigate the stability of the Pt/Vinatech and Pt/Vulcan, a cycling degradation test for a single cell was conducted between 0.6 and 1 V at a scan rate of 50 mV/s (Fig. 8). After a 3k potential cycle, the performance of the fuel cell with Pt/Vinatech increased to 1.7 % in terms of the current density (1.58 A/cm2) (Fig. 8a) at 0.6 V, as well as the power density (Fig. S7), whereas that with Pt/Vulcan (Fig. 8b) and commercial Pt/carbon decreased to 1.38 A/cm2 and 1.33 A/cm2, respectively (Fig. 8c, d). The initial increase in the performance of the Pt/Vinatech could indicate that initially, all Pt NPs, especially inside the porous cavity of the carbon, were not exposed to the catalytic reaction and did not participate in it due to the large pore depth of the Vinatech carbon, but it is expected that these NPs were activated after the gradual cycling test. This can also be explained by the ECSA behavior before and after the MEA cycling test (Fig. S8). After 10k potential cycles, the current density of the Pt/Vinatech started to be decreased similar to Pt/Vulcan and commercial Pt/C. After 30k potential cycles, the Pt/Vinatech showed a reduction (81.5%) in the performance, which is similar to that for the Pt/Vulcan (80.1%), but still showed the highest current density (1.26 A/cm2) (Fig. 8e). The decreased interparticle distance63,64 of dense and small Pt NPs65 may promote the formation of large NPs via aggregation due to the Ostwald ripening mechanism, resulting in a deteriorated cell performance for the Pt/Vinatech owing to a decline in the Pt surface area (Fig. 8f above schematic)63. Nevertheless, the Pt/Vinatech showed excellent fuel cell durability due to the uniform distribution and size of the Pt NPs in the carbon matrix (Fig. 8f below schematic). Furthermore, compared to those for the commercial Pt/C, both catalysts using Pt prepared with FBR-ALD showed better performance and stability due to the homogeneously deposited Pt NPs on both carbons, which was also maintained after the stability testing, according to the TEM analysis (Fig. S9). The cell performance resulting from their well-dispersed characteristics can also be supported by their efficient charge transfer measured by EIS and HRF (Fig. S10). Thus, the FBR-ALD technique is an efficient approach to synthesize uniform Pt catalysts depending on the functionalized surface of the carbon substrate to improve MEA performance and long-term durability.

## Conclusions

In summary, the synthesis of Pt NPs with 30 wt% Pt loading was conducted on two different carbon supports, Vinatech and Vulcan, by using the FBR-ALD method. The nucleation of the Pt NPs was influenced by the textural properties (e.g., surface area, porosity, and pore volume), structural surface defects and carbon functional groups. The structural characterization showed that an improved uniformity and denser Pt dispersion formed on the Vinatech compared to those for the Vulcan at the same weight percent due to its higher surface area with a large pore volume, abundant structural defects and more oxygen functional groups. The uniform architecture of the Pt/Vinatech resulted in a higher ECSA than those of the Pt/Vulcan and commercial catalyst. Finally, the MEA fuel cell performance showed that Pt/Vinatech needed a high Nafion® content due to its densely dispersed Pt NPs. At an optimized Nafion® content, the highest MEA performance was found for the Pt/Vinatech compared to those for the Pt/Vulcan and commercial samples due to its higher ECSA resulting from the uniform and dense ALD-Pt dispersion on the Vinatech carbon support. In fact, the Pt catalysts using FBR-ALD possessed significant long-term stability for the MEA test compared to commercial samples. This study can be a guideline for synthesizing Pt NPs on carbons using the dry ALD process in the catalyst field of PEMFC stacks. In addition, selection of an effective carbon and deposition characteristics for the NPs that are optimized for the carbon properties can enhance the electrochemical and fuel cell performance and provide a way to improve the efficiency and, ultimately, commercialize PEMFCs.

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## Acknowledgements

This work was supported by the Global Frontier R&D Program (2013-073298) on Center for Hybrid Interface Materials (HIM) funded by the Ministry of Science, ICT and Future Planning, and partially supported by the National Research Foundation of Korea (NRF) grant funded by the Korea government (MSIT) (No. 2020R1A2C1014841). The authors would like to thank Dr. Jong-Seong Bae, Miss Jong-Ah Chae, and Miss Seong-Hee Jeong for help with XPS, TEM, and BET investigations.

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Lee, W., Bera, S., Kim, C.M. et al. Synthesis of highly dispersed Pt nanoparticles into carbon supports by fluidized bed reactor atomic layer deposition to boost PEMFC performance. NPG Asia Mater 12, 40 (2020). https://doi.org/10.1038/s41427-020-0223-x

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