# Robust Ruthenium Catalysts Supported on Mesoporous Cyclodextrin-Templated TiO2-SiO2 Mixed Oxides for the Hydrogenation of Levulinic Acid to γ-Valerolactone

Cédric Decarpigny, Sébastien Noël, Ahmed Addad, Anne Ponchel, Eric Monflier, Rudina Bleta

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Cédric Decarpigny, Sébastien Noël, Ahmed Addad, Anne Ponchel, Eric Monflier, et al. Robust Ruthenium Catalysts Supported on Mesoporous Cyclodextrin-Templated TiO2-SiO2 Mixed Oxides for the Hydrogenation of Levulinic Acid to γ-Valerolactone. International Journal of Molecular Sciences, 2021, 22 (4), pp.1721. 10.3390/ijms22041721. hal-03137699

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# Robust Ruthenium Catalysts Supported on Mesoporous Cyclodextrin-Templated TiO₂-SiO₂ Mixed Oxides for the Hydrogenation of Levulinic Acid to γ-Valerolactone

Cédric Decarpigny<fnref n="1" />, Sébastien Noël<fnref n="1" /> ID, Ahmed Addad<fnref n="2" />, Anne Ponchel<fnref n="1" /> ID, Eric Monflier<fnref n="1" /> ID
and Rudina Bleta<fnref n="1" />,*, ID

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**Citation:** Decarpigny, C.; Noël, S.; Addad, A.; Ponchel, A.; Monflier, E.; Bleta, R. Robust Ruthenium Catalysts Supported on Mesoporous Cyclodextrin-Templated TiO₂-SiO₂ Mixed Oxides for the Hydrogenation of Levulinic Acid to γ-Valerolactone.
*Int. J. Mol. Sci.* **2021**, *22*, 1721.
https://doi.org/10.3390/ijms22041721

Academic Editor: Antonino Mazzaglia
Received: 18 December 2020
Accepted: 4 February 2021
Published: 9 February 2021

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**Copyright:** © 2021 by the authors.
Licensee MDPI, Basel, Switzerland.
This article is an open access article distributed under the terms and conditions of the Creative Commons Attribution (CC BY) license (https://creativecommons.org/licenses/by/4.0/).

**Abstract:** In this paper, we present a versatile template-directed colloidal self-assembly method for the fabrication in aqueous phase of composition-tuned mesoporous RuO₂@TiO₂-SiO₂ catalysts. Randomly methylated β-cyclodextrin/Pluronic F127 supramolecular assemblies were used as soft templates, TiO₂ colloids as building blocks, and tetraethyl orthosilicate as a silica source. Catalysts were characterized at different stages of their synthesis using dynamic light scattering, N₂-adsorption analysis, powder X-ray diffraction, temperature programmed reduction, high-resolution transmission electron microscopy, high-angle annular bright-field and dark-field scanning transmission electron microscopy, together with EDS elemental mapping. Results revealed that both the supramolecular template and the silica loading had a strong impact on the pore characteristics and crystalline structure of the mixed oxides, as well as on the morphology of the RuO₂ nanocrystals. Their catalytic performance was then evaluated in the aqueous phase hydrogenation of levulinic acid (LA) to γ-valerolactone (GVL) under mild conditions (50 °C, 50 bar H₂). Results showed that the cyclodextrin-derived catalyst displayed almost quantitative LA conversion and 99% GVL yield in less than one hour. Moreover, this catalyst could be reused at least five times without loss of activity. This work offers an effective approach to the utilization of cyclodextrins for engineering the surface morphology of Ru nanocrystals and pore characteristics of TiO₂-based materials for catalytic applications in hydrogenation reactions.

**Keywords:** levulinic acid; γ-valerolactone; randomly methylated β-cyclodextrin; sol-gel; mixed oxides; Ru catalyst; aqueous phase hydrogenation

## 1. Introduction

With the growing concerns of accelerated global warming that the world faces today, the production of alternative fuels and renewable chemicals from biomass is an utmost challenge for the global scientific community. In this regard, the search for efficient catalytic routes and sustainable chemical processes to convert biomass into high value chemicals in a cost-effective and environmentally friendly manner is an essential step in the development of biorefinery technologies [1–3].

Among biomass-derived compounds, levulinic acid (LA) has been identified as an important platform chemical that can be obtained from the dehydration of lignocellulose-derived C6 sugars in the presence of mineral acids or ionic liquids. The hydrogenation and subsequent dehydration of LA produces γ-valerolactone (GVL) as its major product, which is considered as a sustainable fuel additive for the replacement of ethanol in ethanol/gasoline blends, in addition to its potential applications in pharmaceutical,

<footnote n="1">¹ University Artois, CNRS, Centrale Lille, ENSCL, Univ. Lille, UMR 8181-UCCS-Unité de Catalyse et Chimie du Solide, F-62300 Lens, France; cedric.decarpigny@univ-artois.fr (C.D.); sebastien.noel@univ-artois.fr (S.N.); anne.ponchel@univ-artois.fr (A.P.); eric.monflier@univ-artois.fr (E.M.)</footnote>

<footnote n="2">² University Lille, CNRS, INRA, ENSCL, UMR 8207-UMET-Unité Matériaux et Transformations, F-59000 Lille, France; ahmed.addad@univ-lille.fr</footnote>

<footnote>* Correspondence: rudina.bleta@univ-artois.fr; Tel.: +33-3-21-79-17-40</footnote>
perfume, and food industries, as well as its wide uses as a green solvent for biomass
conversion [4].

The catalytic reduction of LA with hydrogen was first reported in 1930 by Schuette and Thomas [5], who showed that an 87% yield in GVL could be achieved in organic solvent with a PtO₂ catalyst after 44 h at room temperature and 3 bar H₂. Since then, many metal catalysts have been reported in the literature and among them, Ru has proven to be the most suitable for the hydrogenation of LA to GVL in aqueous phase [6–11], whereas Pd and Pt were found to be more active in the hydrogenation of ketones under gas phase conditions [12]. Michel et al. [13] correlated the better activity of Ru in aqueous phase to its higher degree of oxyphilicity with respect to Pd and Pt. Indeed, by combining DFT calculations and experimental data, it was shown that the interaction of water molecules with the carbonyl groups of LA adsorbed on the Ru surface could considerably lower the energy barrier of the reaction pathway, facilitating the hydrogenation of carbonyl groups [13–15]. Moreover, the increase in the amount of hydrogen atoms resulting from water dissociation on the Ru (0001) surface was identified as an additional factor responsible for the increased reaction rates [16].

The catalytic performance of Ru-based catalysts can be further improved by deposit-
ing the metal particles on a solid support. In this regard, mesoporous materials have
been widely used as versatile supports owing to their high surface areas and large pore
volumes that provide numerous active sites on the catalyst surface [17–20]. In particular,
Ru supported on activated carbon (Ru/C) was found to be highly effective for this reaction,
achieving 100% LA conversion and 97.5% selectivity to GVL after 50 h at room tempera-
ture [21]. However, this catalyst also demonstrated rapid deactivation during the recycling
process.

In an effort to increase the catalyst stability, mesoporous metal oxides, such as γ-Al₂O₃, SiO₂, ZrO₂, and TiO₂ have emerged as promising alternatives to activated carbon owing to their high mechanical and thermal stability [22–26]. However, some of them show limited stability under acidic and hydrothermal conditions. Thus, SiO₂ easily converts into a gel, while γ-Al₂O₃ has the tendency to transform into boehmite (AlO(OH)) at pH values between 4.5 and 11.5 [21,22]. On the other hand, TiO₂ and ZrO₂ have shown the highest stability in this reaction [23–25], despite the fact that Zr(OH)₄ is generally more stable in water with respect to ZrO₂ [26]. The superior activity of Ru/TiO₂ was linked to the electronic properties of TiO₂ which are favorable to the enhancement of metal support interactions and the formation of highly active Ru species in the selective hydrogenation of the carbonyl group [27–31].

Cyclodextrins (CDs) are water-soluble cyclic oligosaccharides composed of (α-1,4)-linked α-D-glucopyranose units presenting an internal hydrophobic cavity and a hydrophilic exterior surface. Alpha-, beta-, and gamma-CDs with respectively six, seven, and eight glucose units in the ring are the most common native cyclodextrins and among them, β-CD has received the greatest interest due to its high binding affinity and cost effectiveness [32,33]. Randomly methylated β-CD (RaMeβCD) is one of the most widely used β-CD derivatives with a degree of substitution (DS) of about 12.6 and a molecular structure that confers to these oligosaccharide surface-active properties and high solubility in water (>500 mg/mL). Although the possibility of utilizing native or modified cyclodextrins as structure-directing agents in the synthesis of silica nanostructures has been explored so far [34–37], a smaller number of reports have been devoted to the practical applications of these materials. Recently, we have developed an efficient CD-assisted colloidal approach to prepare hierarchically porous silica [37], as well as mesoporous alumina [38,39] and titania materials [40,41] with enhanced activity in photocatalysis [40–42], heterogeneous catalysis [43–46], and biocatalysis [47]. In particular, RuO₂@TiO₂ catalysts with tunable porosities, prepared using RaMeβCD-Pluronic P123 assemblies as a supramolecular template, gave excellent activity in the selective hydrogenation of methyl oleate to methyl stearate under mild reaction conditions [43].
Conventional TiO₂ simple oxides still encounter limitations for application in het-
erogeneous catalysis due to the agglomeration of titania particles that generally imply
inefficient mass transfer and poor pore accessibility, therefore declining the catalytic rate.
Indeed, as pointed out by several authors, TiO₂ undergoes sintering at high temperatures
due to the coarsening and growth of metastable anatase and brookite crystallites, which
further transform to rutile when a critical size is reached [48]. Such phase transformation
is non-reversible due to the thermodynamic stability of the rutile phase which generally
provokes a collapse of the nanostructure [49,50]. In an attempt to overcome this problem,
the embedding of TiO₂ particles in a porous and high surface area SiO₂ matrix is an effec-
tive way to avoid particle aggregation. The uniform dispersion of titania particles in silica
is nevertheless challenging due to the differences in hydrolysis and condensation rates of
titanium and silicon alkoxides in water, which are identified as major limiting factors in
the preparation of mixed TiO₂-SiO₂ mesoporous oxides.

In this study, a sophisticated CD-directed colloidal self-assembly strategy is demon-
strated for the first time to tune the assembly process yielding uniform dispersion of TiO2
nanoparticles in a highly porous SiO2 matrix. Importantly, the porous matrix provides
a confined environment not only to prevent TiO2 agglomeration, but also to control the
growth process of Ru-catalyst yielding nanoparticles with different sizes and shapes (spher-
ical, plate-like, lozenge-like, and rod-like). As a proof of concept, these catalysts were found
to be particularly active in the aqueous phase hydrogenation of LA to GVL under mild
reaction conditions, therefore opening new perspectives for the use of CD-based assemblies
in the synthesis of high-performance catalysts.

**2. Results**

2.1. *Method for the Preparation of the Catalysts*

The mesoporous TiO₂ and TiO₂-SiO₂ supported RuO₂ catalysts were prepared according to the procedure depicted in Figure 1. First, a hybrid organic-inorganic material was obtained in aqueous phase by self-assembly of sol-gel synthesized TiO₂ nanoparticles around the supramolecular assemblies formed between the randomly methylated β-CD (RaMeβCD) and the Pluronic F127. Then, the hybrid mesophase was either subjected to calcination at 500 °C to yield a mesoporous TiO₂ material (Figure 1A) or further coated with a silica shell using the tetraethyl orthosilicate (TEOS) as a silica source (Figure 1B). By varying the TEOS concentration in the titania hydrosol, mesoporous titania-silica composites (TiO₂-SiO₂) with different silica loadings and porosities were obtained after template removal at 500 °C. In both syntheses, the obtained mesoporous supports were subsequently impregnated with an aqueous solution of ruthenium nitrosyl nitrate, followed by a thermal treatment at 400 °C under air flow, affording mesoporous RuO₂@TiO₂ and RuO₂@TiO₂-SiO₂ heterostructures.

## 2.2. *Characterization of the Supports*

To gain insight into the coassembly behavior of Pluronic F127 (PEO₁₀₆PPO₇₀PEO₁₀₆) and RaMeβCD, DLS measurements were carried out at 25 °C. The Pluronic F127 concentrations used were above the critical micelle concentration (CMC) (0.7% *w/v* at 25 °C) [51]. Figure 2 shows the intensity size distributions of mixtures prepared with 10% *w/v* F127 and increasing amounts of RaMeβCD, from 10 to 110 mg mL⁻¹. In the F127 solution prepared without RaMeβCD, the main scattering species are polymer oligomers and micelles with an average hydrodynamic diameter of 4.9 nm and 47 nm respectively. Upon addition of increasing amounts of RaMeβCD, the size of the micelles increases progressively from 59 nm (10 mg mL⁻¹ RaMeβCD) to 98 nm (50 mg mL⁻¹ RaMeβCD). Such a micellar growth may be explained by the ability of this cyclodextrin to locate preferentially at the interface layer of F127 micelles in interaction with the hydrophobic PPO blocks [38]. As a result of these interactions, the aggregation number of micelles increases, and interfaces tend to become more flexible inducing morphological changes when a certain packing density is reached. Hence, at 80 mg mL⁻¹ RaMeβCD (RaMeβCD/F127 = 7.8), the decrease
of the scattering intensity indicated the beginning of the restructuration of the micelles, which led to their total dissociation at 110 mg mL⁻¹ RaMeβCD. Note that the micellar breakup occurred when the cyclodextrin was in large excess to the copolymer. Indeed, at 3% *w/v* F127, a 30 mg mL⁻¹ RaMeβCD loading (RaMeβCD/F127 = 9.6) was sufficient to observe the micelle rupture, while at 15% *w/v* F127, micelles remained intact at a RaMeβCD loading as high as 110 mg mL⁻¹ (RaMeβCD/F127 = 7.0) (Figure S1, ESI). Typically, the restructuration of interfaces was found to occur for RaMeβCD/F127 molar ratios higher than 7. Based on these results, the template chosen for the preparation of the supported catalysts was the mixture composed of 10% *w/v* Pluronic F127 and 50 mg mL⁻¹ RaMeβCD (RaMeβCD/F127 = 4.8), as in this concentration range micelles maintained their structural integrity.

<figure><img src="image_5.png" /><figcaption>**Figure 1.** Schematic illustration of the colloidal approach for the preparation of the RuO₂@TiO₂ (A) and RuO₂@TiO₂-SiO₂ (B) catalysts.</figcaption></figure>

<figure><img src="image_6.png" /><figcaption>**Figure 2.** Dynamic light scattering (DLS) plots of the micellar solution of Pluronic F127 (10% *w/v*) prepared with increasing concentrations of RaMeβCD from 10 mg mL⁻¹ to 110 mg mL⁻¹.</figcaption></figure>

Figure 3A shows the N₂-adsorption isotherms and corresponding pore size distributions (inset) of the TiO₂ material and TiO₂-SiO₂ composites prepared using the colloidal approach (Figure 1). All solids displayed a type IV isotherm with a type H1 hysteresis
loop characteristic of mesoporous materials. The adsorption isotherm of the template-free sol-gel TiO₂ (TiO₂-sg) showed a capillary condensation step that started at a relative pressure (P/P₀) of about 0.45, consistent with the formation of compact microstructures (0.03 cm³ g⁻¹ pore volume and less than 2 nm diameter). Upon addition of the RaMeβCD-Pluronic F127 assemblies, a steep rise in the N₂ uptake occurred at P/P₀ > 0.7 indicating the formation of larger mesopores with 7.4 nm pore diameters. Moreover, the increase in both surface area (from 21 to 80 m² g⁻¹) and pore volume (from 0.03 to 0.20 cm³ g⁻¹) (Table 1) is a signature of the template effect, as evidenced also in the case of bare silica (Figure S2, Table S1, ESI). Interestingly, the textural characteristics were further improved through sol-gel polymerization of the TEOS around the network formed by the conjunction of RaMeβCD-Pluronic F127 template and TiO₂ nanoparticles. Indeed, by varying the composition of silica in the composite material, it was possible to tune the average pore diameter in a broad range between 10.9 nm and 20.4 nm (Table 1).

<table><caption>**Table 1.** Structural and textural characteristics of the TiO₂ materials and TiO₂-SiO₂ composites after calcination at 500 °C.</caption><thead><tr><th rowspan="2">Sample</th><th rowspan="2">S<sub>BET</sub> <sup>a</sup><br>(m<sup>2</sup> g<sup>-1</sup>)</th><th rowspan="2">V<sub>cum</sub> <sup>b</sup><br>(cm<sup>3</sup> g<sup>-1</sup>)</th><th rowspan="2">PS <sup>c</sup><br>(nm)</th><th colspan="3">Crystallite Size <sup>d</sup> (nm)</th></tr><tr><th>Anatase TiO<sub>2</sub></th><th>Brookite TiO<sub>2</sub></th><th>Rutile TiO<sub>2</sub></th></tr></thead><tbody><tr><td>TiO<sub>2</sub>-sg</td><td>21 ± 1</td><td>0.030 ± 0.002</td><td>&lt;2.0 ± 0.4</td><td>36.4 ± 2.9</td><td>18.7 ± 1.5</td><td>60.4 ± 4.8</td></tr><tr><td>TiO<sub>2</sub>-ns</td><td>80 ± 4</td><td>0.20 ± 0.01</td><td>7.4 ± 1.5</td><td>11.0 ± 0.9</td><td>4.5 ± 0.4</td><td>11.5 ± 0.9</td></tr><tr><td>TiO<sub>2</sub>-SiO<sub>2</sub> 3:1-ns</td><td>169 ± 8</td><td>0.49 ± 0.02</td><td>11.1 ± 2.2</td><td>10.3 ± 0.8</td><td>4.4 ± 0.4</td><td>9.5 ± 0.8</td></tr><tr><td>TiO<sub>2</sub>-SiO<sub>2</sub> 3:2-ns</td><td>198 ± 10</td><td>0.93 ± 0.05</td><td>18.1 ± 3.6</td><td>6.2 ± 0.5</td><td>2.7 ± 0.2</td><td>-</td></tr><tr><td>TiO<sub>2</sub>-SiO<sub>2</sub> 3:3-ns</td><td>193 ± 10</td><td>1.17 ± 0.06</td><td>24.0 ± 4.8</td><td>6.1 ± 0.5</td><td>2.7 ± 0.2</td><td>-</td></tr></tbody></table>

X-ray diffraction (XRD) patterns also confirmed that both the supramolecular template and silica loading had an impact on the crystalline properties of titania-based solids (Figure 3B). Indeed, in the TiO₂-sg material, the intense sharp peak at 2θ = 27.4° is characteristic of the (110) plane of the rutile polymorph (R) (JCPDS card no. 00-034-0180), which results from the transformation of metastable anatase (A) (JCPDS card no. 00-021-1272) and brookite (B) (JCPDS card no. 01-076-1934) during calcination. The crystallite sizes of those polymorphs determined from the Scherrer formula were 36 nm (A), 19 nm (B), and 60 nm (R). The rapid growth of rutile crystallites may be attributed to the high level of aggregation of particles in the sol-gel TiO₂ material, facilitating the contact between neighboring grains. Indeed, as shown previously by Zhang et al. [52,53], when the anatase particles are in intimate contact with each other, the interfaces of the contacting grains provide the nucleation sites of the rutile phase. Once the nucleation is initiated, rutile particles grow very fast and the phase transformation spreads quickly throughout the whole material. Noticeably, when the RaMeβCD-Pluronic F127 assemblies were used as a template, the intensities of rutile reflections were markedly attenuated, and they totally disappeared when silica was incorporated to the titania network. Moreover, the broadening of the XRD peaks is consistent with the formation of smaller particles resulting from the delay in phase transformation. Thus, the size of crystallites determined from the Scherrer formula decreased from 36.4 nm (A) and 18.7 nm (B) for TiO₂-sg to 11.0 nm (A) and 4.5 nm (B) for TiO₂-ns and further to 6.1 (A) and 2.7 nm (B) for TiO₂-SiO₂ 3:3-ns. Such a decrease in the size of crystallites also explains the increase in the specific surface area and pore volume of TiO₂-SiO₂ composites (Table 1).

Taken together, these data indicate that both the RaMeβCD-F127 assemblies and the silica network play a key role in inhibiting crystal growth and stabilizing anatase and brookite polymorphs with respect to the rutile.

<footnote><sup>a</sup> Specific surface area determined in the relative pressure range 0.1-0.25; <sup>b</sup> cumulative pore volume and <sup>c</sup> average pore size resulting from BJH calculations, <sup>d</sup> crystallite size calculated using the Scherrer equation.</footnote>
<figure><img src="image_7.png" /><figcaption>**Figure 3.** N₂-adsorption isotherms and corresponding pore size distributions (inset) (A) and XRD patterns (B) of TiO₂-sg (a), TiO₂-ns (b), TiO₂-SiO₂ 3:1-ns (c), TiO₂-SiO₂ 3:2-ns (d), TiO₂-SiO₂ 3:3-ns (e). The “A”, “B” and “R” denote the anatase, brookite and rutile phases respectively.</figcaption></figure>

### 2.3. Characterization of the Supported Catalysts

To further investigate the impact of RuO₂ particles on the textural and structural characteristics of supported catalysts, N₂-adsorption and XRD analyses were carried out. From the N₂-adsorption isotherms (Figure 4A), it can be seen that all TiO₂-based materials retained their mesoporous structure after dispersion of the active elements. As a general trend, the specific surface area, pore volume and pore size decreased slightly after dispersion of RuO₂ particles while the pore architecture was not altered, which could be beneficial for the diffusion of reactants and products during the catalytic process. For instance, the surface area, pore volume and pore diameter were determined to be 156 m²/g, 0.72 cm³/g and 15.1 nm respectively for the RuO₂@TiO₂-SiO₂ 3:3-ns catalyst (Table 2) and
193 m²/g, 1.17 cm³/g and 24.0 nm respectively for the corresponding TiO₂-SiO₂ 3:3-ns support (Table 1). It is noteworthy to mention that all those catalysts had much better textural characteristics compared to other crystalline TiO₂-supported Ru catalysts reported in the literature [26] due to the small-sized TiO₂ particles resulting from the high hydrolysis ratio employed under our synthesis conditions (H₂O/Ti = 88).

<table><caption>**Table 2.** Characteristics of supported RuO₂@TiO₂ and RuO₂@TiO₂-SiO₂ catalysts after thermal treatment at 400 °C.</caption><thead><tr><th>Sample</th><th>S<sub>BET</sub><sup>a</sup><br>(m<sup>2</sup> g<sup>-1</sup>)</th><th>V<sub>cum</sub><sup>b</sup><br>(cm<sup>3</sup> g<sup>-1</sup>)</th><th>PS<sup>c</sup><br>(nm)</th><th>RuO<sub>2</sub> Size<sup>d</sup><br>(nm)</th></tr></thead><tbody><tr><td>RuO<sub>2</sub>@TiO<sub>2</sub>-sg</td><td>8 ± 0.4</td><td>0.015 ± 0.00</td><td>&lt;2.0 ± 0.4</td><td>15.8 ± 1.6</td></tr><tr><td>RuO<sub>2</sub>@TiO<sub>2</sub>-ns</td><td>65 ± 3.2</td><td>0.18 ± 0.01</td><td>6.1 ± 1.2</td><td>9.9 ± 1.0</td></tr><tr><td>RuO<sub>2</sub>@TiO<sub>2</sub>-SiO<sub>2</sub> 3:1-ns</td><td>162 ± 8.1</td><td>0.43 ± 0.021</td><td>10.6 ± 2.1</td><td>9.0 ± 0.9</td></tr><tr><td>RuO<sub>2</sub>@TiO<sub>2</sub>-SiO<sub>2</sub> 3:2-ns</td><td>138 ± 6.9</td><td>0.50 ± 0.03</td><td>15.0 ± 3.0</td><td>-</td></tr><tr><td>RuO<sub>2</sub>@TiO<sub>2</sub>-SiO<sub>2</sub> 3:3-ns</td><td>156 ± 7.8</td><td>0.72 ± 0.04</td><td>15.1 ± 3.0</td><td>-</td></tr></tbody></table>

Compared to bare TiO₂ and TiO₂-SiO₂ supports, the XRD patterns of supported catalysts (Figure 4B) revealed the existence of two additional reflection lines at 2θ = 27.8° and 34.9° originating from the (110) and (101) planes respectively of the tetragonal RuO₂ (JCPDS 00-043-1027). Note that among the five catalysts, RuO₂@TiO₂-sg showed the highest RuO₂ reflection intensities indicating larger particle sizes with an average diameter of 15.8 nm, as determined from the line broadening of the (110) reflection. This result is consistent with the epitaxial growth of RuO₂ phase over rutile-TiO₂, which is the predominant polymorph in the TiO₂-sg support. Indeed, the (110) and (101) planes of RuO₂ overlap with the (110) and (101) planes of rutile-TiO₂ due to the structural matching between these two phases, both of which share a tetragonal lattice symmetry and have very similar lattice parameters (a = 4.59 Å, c = 2.96 Å for rutile-TiO₂ and a = 4.49 Å, c = 3.10 Å for RuO₂) [54]. Similarly to the supramolecular template, the sol-gel polymerization of TEOS around TiO₂ particles permitted stabilization of anatase and brookite with respect to rutile. RuO₂ particles dispersed over this support were well-crystallized, as confirmed by the sharp peaks originating from the reflection planes of tetragonal RuO₂ (Figure S3, ESI). On the other hand, the combined use of the supramolecular RaMeβCD-Pluronic F127 template and TEOS resulted in a further broadening of the reflection peaks of RuO₂ and a reduction in the size of RuO₂ crystallites which decreased from 15.8 nm (RuO₂@TiO₂-sg) to 9.9 nm (RuO₂@TiO₂-ns) and to 9.0 nm (RuO₂@TiO₂-SiO₂ 3:1-ns) (Table 2).

Transmission electron microscopy (TEM) images confirmed that the Ru@TiO₂-sg catalyst was composed of large RuO₂ agglomerates with irregular sizes varying from 20 to 50 nm in diameter (dark regions) dispersed in a fully dense titania microstructure (white regions) (Figure 5A). Titania particles showed lattice fringes with 0.354 nm and 0.326 nm interlayer distances corresponding to anatase (101) and rutile (110) planes respectively, in line with XRD results (Figure 5B). Moreover, elongated heterogeneous structures were also identified (red arrows), consistent with the epitaxial growth of RuO₂ crystallites over rutile-TiO₂ (Figure 5C,D). Importantly, the nanostructured RaMeβCD-templated TiO₂-ns support provided a more uniform dispersion of the active phase, indicating formation of Ru clusters with an average diameter of 15–20 nm located either on the external surface of titania particles or encapsulated inside the pores (Figure 5E,F). The numerous void spaces observed between the TiO₂ particles (white regions) confirm the important role played by the RaMeβCD-swollen F127 micelles in the pore expansion, in agreement with N₂-adsorption results.

<footnote><sup>a</sup> specific surface area determined in the relative pressure range 0.1–0.25, <sup>b</sup> cumulative pore volume and <sup>c</sup> average pore size resulting from Barrett, Joyner, and Halenda (BJH) calculations; <sup>d</sup> RuO₂ crystallite size determined using the Scherrer equation.</footnote>
<figure><img src="image_8.png" /><figcaption>**Figure 4.** N₂ adsorption isotherms and corresponding pore size distributions (inset) (A) and XRD patterns (B) of RuO₂@TiO₂-sg (a), RuO₂@TiO₂-ns (b), RuO₂@TiO₂-SiO₂ 3:1-ns (c), RuO₂@TiO₂-SiO₂ 3:2-ns (d), and RuO₂@TiO₂-SiO₂ 3:3-ns (e). “R” denotes the rutile phase.</figcaption></figure>

High-angle annular bright-field and dark-field scanning transmission electron microscopy (HAABF- and HAADF-STEM, respectively) images together with EDS mappings were further used to examine the distribution of Ti, Si, Ru, and O elements in the three RuO₂@TiO₂-SiO₂-ns catalysts. Note that the bright particles in the HAADF-STEM images are those that contain the heaviest element, i.e., Ru.

As shown in Figure 6, the Ti, Si, and O elements were distributed evenly throughout the selected area of all catalysts. However, the growth of RuO₂ nanostructures was different depending on the amount of silica incorporated within the titania network. Indeed, the
$RuO_2@TiO_2-SiO_2$ 3:1-ns catalyst prepared with the lowest silica loadings provided spherical particles that tended to agglomerate into grapes (Figure 6A and Figure S4, ESI). A closer examination by HR-TEM revealed that Ru nanostructures were composed of globular Ru clusters with 5 nm diameter agglomerated into larger particles with an average size of 20–30 nm (Figure S5, ESI). Importantly, the addition of increasing amounts of silica to the titania network ($TiO_2-SiO_2$ 3:2-ns and $TiO_2-SiO_2$ 3:3-ns solids) involved a more uniform dispersion of Ru particles as well as a shape transformation from circular particles to heterogeneous structures composed of plate-like or lozenge-shaped crystals having an average particle size of 40–50 nm (Figure 6B,C and Figure S7, ESI). Moreover, in some local regions, it can be seen that $RuO_2$ clusters tend to further aggregate, forming rod-like particles of 50–100 nm length and 20–40 nm width (Figure S6, ESI).

<figure><img src="image_9.png" /><figcaption>**Figure 5.** Representative TEM images of Ru@$TiO_2$-sg (A–D) and Ru@$TiO_2$-ns (E,F). Red arrows indicate the epitaxial growth of $RuO_2$ crystallites over rutile-$TiO_2$-sg (B–D) and formation of Ru clusters with an average diameter of 15–20 nm over $TiO_2$-ns (F).</figcaption></figure>
<figure><img src="image_10.png" /><figcaption>**Figure 6.** HAABF- (a) and HAADF-STEM (b) images together with corresponding energy dispersive X-ray (EDX) elemental mapping of Ti (c), Si (d), Ru (e), and O (f) for RuO₂@TiO₂-SiO₂ 3:1-ns (A), RuO₂@TiO₂-SiO₂ 3:2-ns (B), and RuO₂@TiO₂-SiO₂ 3:3-ns (C) catalysts. Insets in subfigures b show a higher magnification of RuO₂ particles.</figcaption></figure>
Temperature programmed reduction (TPR) measurements further illustrate the differ-
ent reducibility behavior of RuO₂ on different supports (Figure 7). Thus, RuO₂@TiO₂-sg
presented a broad peak beginning at 230 °C and extending up to 380 °C assigned to the re-
duction of Ru⁴⁺ to Ru⁰ (Figure 7A). Such a high reduction temperature is likely attributable
to the formation of epitaxial layers of RuO₂ in strong interaction with rutile-TiO₂, in line
with the XRD and TEM results. A clear shift of this temperature to lower values was
observed on the RuO₂@TiO₂-ns catalyst, which displayed two detached peaks suggesting
formation of two different types of Ru species (Figure 7B) [43]. The first peak, centered at
163 °C, may be related to the reduction of surface particles that interact weakly with titania
surfaces and the second one, centered at 196 °C extending up to 240 °C, may be attributed
to the reduction of RuO₂ particles incorporated within the pores. On the other hand, RuO₂
particles supported over mixed oxides globally displayed lower reduction temperatures
in the range of 180–185 °C which did not exceed 200 °C (Figure 7C–E). Moreover, as the
silica content increased, the material became more porous and the shoulder on the primary
reduction peak disappeared, suggesting the formation of one type of particle incorporated
within the pores. It is worthy to note that the RuO₂@TiO₂-SiO₂ 3:3-ns catalyst displayed a
lower reduction temperature and narrower peak compared to the RuO₂@TiO₂-SiO₂ 3:3-sg
catalyst (Figure S8, ESI) indicating higher homogeneity and readily reducible RuO₂ parti-
cles. Notably, no significant reduction of the support was observed when the temperature
was raised to 800 °C (Figure S8, ESI).

<figure><img src="image_11.png" /><figcaption>**Figure 7.** Temperature programmed reduction (TPR) patterns of RuO₂@TiO₂-sg (A), RuO₂@TiO₂-ns (B), RuO₂@TiO₂-SiO₂ 3:1-ns (C), RuO₂@TiO₂-SiO₂ 3:2-ns (D), and RuO₂@TiO₂-SiO₂ 3:3-ns (E).</figcaption></figure>
## 2.4. Catalytic Tests

The catalytic performances of supported catalysts were investigated in the hydrogenation of levulinic acid (LA) to γ-valerolactone (GVL). Prior to the catalytic reaction, $RuO_2$ was reduced in metallic Ru using a 5% $H_2$/Ar flow at 400 °C for 2 h, and then immediately transferred in autoclave. All experiments were performed at 50 °C under a hydrogen pressure of 50 bar.

The efficient catalytic conversion of levulinic acid to γ-valerolactone in aqueous phase involves two main steps: first the hydrogenation of LA, yielding 4-hydroxypentanoic acid (4-HPA) as an intermediate, followed by the subsequent cyclization of the latter forming GVL (see Table 3) [26,55–58]. Figure 8 shows concentration versus time profiles for LA and GVL obtained with the different catalysts during the first 60 min of reaction. Ru deposited on $TiO_2-SiO_2$ 3:3-sg composite is added for comparison. At 2.5 wt.% Ru loading, all catalysts provided a sufficient amount of active sites to initiate the hydrogenation reaction and were able to give near quantitative LA conversions with GVL yields comprised between 72% and 99%. In all reaction mixtures, the only intermediate product detected was 4-HPA (see ¹H NMR spectra Figures S9 and S10, ESI) in agreement with literature data for reactions performed in water [13,15,59]. Other intermediates such as α-angelicalactone or GVL hydrogenation products (i.e., 1,4-pentanediol or 2-methyltetrahydrofuran) were not observed under our reaction conditions, indicating selectivity towards GVL formation.

<table><caption>**Table 3.** Catalytic hydrogenation of LA to GVL with the different Ru-based catalysts<sup>a</sup>.</caption><thead><tr><th>Entry</th><th>Catalyst</th><th>TiO<sub>2</sub> (%)<sup>b</sup></th><th>SiO<sub>2</sub> (%)<sup>b</sup></th><th>LA Conversion (%)<sup>c</sup></th><th>GVL Yield (%)<sup>c</sup></th><th>Productivity (mol<sub>GVL</sub> g<sup>-1</sup> metal h<sup>-1</sup>)<sup>d</sup></th></tr></thead><tbody><tr><td>1</td><td>TiO<sub>2</sub>-ns</td><td>100</td><td>0</td><td>&lt;3</td><td>0</td><td>-</td></tr><tr><td>2</td><td>TiO<sub>2</sub>-SiO<sub>2</sub> 3:3-ns</td><td>66</td><td>34</td><td>&lt;3</td><td>0</td><td>-</td></tr><tr><td>3</td><td>Ru@TiO<sub>2</sub>-sg</td><td>100</td><td>0</td><td>65</td><td>46</td><td>4.0434</td></tr><tr><td>4</td><td>Ru@TiO<sub>2</sub>-ns</td><td>100</td><td>0</td><td>79</td><td>58</td><td>5.0983</td></tr><tr><td>5</td><td>Ru@TiO<sub>2</sub>-SiO<sub>2</sub> 3:1-ns</td><td>87</td><td>13</td><td>82</td><td>75</td><td>6.5926</td></tr><tr><td>6</td><td>Ru@TiO<sub>2</sub>-SiO<sub>2</sub> 3:2-ns</td><td>76</td><td>24</td><td>88</td><td>76</td><td>6.6805</td></tr><tr><td>7</td><td>Ru@TiO<sub>2</sub>-SiO<sub>2</sub> 3:3-ns</td><td>66</td><td>34</td><td>91</td><td>78</td><td>6.8563</td></tr><tr><td>8</td><td>Ru@TiO<sub>2</sub>-SiO<sub>2</sub> 3:3-sg</td><td>68</td><td>32</td><td>73</td><td>56</td><td>4.9225</td></tr><tr><td>9</td><td>Ru@C</td><td>-</td><td>-</td><td>99</td><td>66</td><td>5.8015</td></tr></tbody></table>

It is interesting to note that both LA conversion and GVL yield were influenced by the nature of the support material. For instance, the highest conversions were achieved with Ru particles supported on mixed $TiO_2-SiO_2$ oxides prepared by the template approach, intermediate activities were found for catalysts supported on nanostructured $TiO_2$, and the lowest LA conversions were obtained with Ru dispersed over $TiO_2$-sg and $TiO_2-SiO_2$-sg supports. A similar tendency was observed also in the GVL yield which increased with silica loading, reaching a maximum of 99% for the Ru@$TiO_2-SiO_2$ 3:2-ns catalyst.

To evaluate the efficiency of different catalysts, activities were then compared after 20 min of reaction time. A compilation of the data is given in Table 3. As expected, the blank $TiO_2$ and $TiO_2-SiO_2$ supports exhibited insignificant catalytic activity due to the

<footnote><sup>a</sup> Reaction conditions: 0.66 g LA (5.68 mmol), 77.6 mg supported catalyst (0.019 mmol Ru), 50 bar $H_2$, 20 mL $H_2O$, temperature 323 K, and reaction time 20 min. <sup>b</sup> Mass % of oxide determined by XRF. <sup>c</sup> Determined by GC using Equations (2) and (3) (see experimental part) and benzaldehyde as an internal standard. <sup>d</sup> Productivity: moles of GVL produced per g of Ru per hour.</footnote>
absence of active sites (entries 1 and 2). The Ru@TiO₂-sg catalyst gave 65% LA conversion and 46% GVL yield with a productivity of 4.0 mol_GVL·g⁻¹ₘetal·h⁻¹ (entry 3). Notably, when the CD-based assemblies were used as template, the GVL yield increased to 58%, affording a productivity of 5.1 mol_GVL·g⁻¹ₘetal·h⁻¹ (entry 4). Interestingly, further improvement in the catalytic performance was noticed upon increasing the silica loading. Indeed, LA conversions obtained with the three Ru@TiO₂-SiO₂-ns catalysts were higher than 80% and GVL yields were between 75% and 78%, giving productivities in the range of 6.59–6.86 mol_GVL·g⁻¹ₘetal·h⁻¹ (entries 5–7). Note that the best results were obtained with Ru@TiO₂-SiO₂ 3:3-ns, affording 91% LA conversion and 78% GVL yield with a productivity of 6.85 mol_GVL·g⁻¹ₘetal·h⁻¹, which is almost 1.65-fold higher than the results obtained with the Ru@TiO₂-sg catalyst. For comparison, Ru@TiO₂-SiO₂ 3:3-sg prepared by conventional sol-gel process gave intermediate activities between Ru@TiO₂-sg and Ru@TiO₂-ns, with a GVL yield of 56% and a productivity of 4.9 mol_GVL·g⁻¹ₘetal·h⁻¹ (entry 8). In comparison, commercial 5%Ru@C gave an almost full LA conversion in the first 20 min, but it produced only 66% GVL yield.

Our results can be compared with those reported by Almeida et al. [60] who obtained 96% LA conversion and 89% GVL yield with a 5%Ru@TiO₂-SiO₂ catalyst after 6 h at 100 °C and 20 atm H₂. However, in this study, the catalytic tests were performed in ethanol, where ethyl levulinate is expected to form as a byproduct through the transesterification of levulinic acid [61]. No data were available however for the reaction performed in water. Using a 5%Cu/γ-Al₂O₃ catalyst, 87% yield of GVL was reached by Putrakumar et al. [62] in gas phase at 265 °C and 30 mL H₂ flow. The catalyst showed good activity during the initial hours of reaction, but tended to deactivate as the reaction time with increased. Jones et al. [63] achieved 90% yield in GVL at 100 °C under 5 bar H₂ with a 1%Ru/C catalyst stabilized by a small amount of PVA (PVA/Ru = 0.1). However, during the recycling experiments, this catalyst showed a decline in activity which was attributed to the removal of PVA from the Ru surface, followed by particle sintering. In another study, Piskun et al. [56] obtained 86% LA conversion and 79% GVL yield with a 1%Ru@TiO₂ catalyst in water after 4 h at 90 °C and 45 bar H₂. As already well-established in the literature, water strongly accelerates the reaction rate with respect to organic solvents as it participates to the hydrogenation of the C=O group of LA by decreasing the energy barrier [13,24]. Moreover, although H₂ is less soluble in water than in organic solvents, the ability of water to promote the hydrogen spillover by transporting H atoms on the catalyst surface appears also to contribute to its enhanced activity [16,64,65].

Overall, our results indicate that both the supramolecular RaMeβCD/F127 assemblies and the silica network have a beneficial effect on the catalytic properties of Ru-based composites. Indeed, comparison of the activities obtained with Ru@TiO₂-ns (entry 4) and Ru@TiO₂-sg (entry 3), as well as with Ru@TiO₂-SiO₂ 3:3-ns (entry 7) and Ru@TiO₂-SiO₂ 3:3-sg (entry 8), clearly reveal the determinant role of the supramolecular template on the catalytic performance of Ru. The higher performance of those catalysts can be largely attributed to a combined effect of improved structural and textural properties of the support and more uniform dispersion of the Ru particles, as confirmed by our XRD, N₂-adsorption, and HR-TEM and HAADF-STEM results. Moreover, the results obtained with mixed oxides also suggest that there is a significant potential for further activity improvement by embedding titania particles within the silica matrix prior to Ru dispersion. The silica network seems to play a key role not only on the characteristics of the support itself, whose pore diameter increased from 7.4 to 24.0 nm, but also on the morphology of Ru particles which transformed from spherical to plate-like, lozenge-like, and rod-like nanocrystals with increased silica loading. Although the thickness of those structures could not be determined from our TEM images, the evolution observed on particle morphology may also have some effects on the catalytic activity through orientation of certain facets of Ru nanocrystals. Indeed, DFT calculations have suggested that Ru nanocrystals with exposed {111} facets were more effective than Ru nanoparticles in catalyzing nitrogen reduction for
ammonia synthesis [66] and have recently shown very beneficial effects on the catalytic activity towards oxygen evolution reactions [67].

<figure><img src="image_12.png" /><figcaption>**Figure 8.** The influence of reaction time on the LA conversion (A) and the GVL yield (B) by various catalysts. Reaction conditions: 0.66 g LA (5.68 mmol), 77.6 mg supported catalyst (0.019 mmol Ru), 50 bar H₂, 20 mL H₂O, temperature 323 K, and reaction time 1 h.</figcaption></figure>

To gain a deeper understanding on the role of the chemical nature of the support material, we also conducted a set of control experiments on other mixed oxides with high surface areas and pore volumes (Table S2, ESI). Results revealed that the catalytic activity of sol-gel and nanostructured Ru@TiO₂-SiO₂ 3:3 catalyst was superior to that of the Ru@TiO₂-Al₂O₃ 3:3 and Ru@SiO₂-Al₂O₃ 3:3 catalysts prepared by a similar colloidal approach using boehmite AlO(OH) particles as precursor of γ-Al₂O₃ [38]. Although SiO₂-Al₂O₃ supports presented the best textural characteristics among the three mixed oxides, LA conversions and GVL yields obtained under the same reaction conditions (50 °C, 50 bar H₂, 20 min) were found to evolve in the order Ru@TiO₂-SiO₂ 3:3 > Ru@TiO₂-Al₂O₃ 3:3 > Ru@SiO₂-Al₂O₃ 3:3 (Figure S11, ESI). This means, nonetheless, that the surface areas and pore volumes are not the only factors that explain the marked improvement in the catalytic performance of Ru@TiO₂-SiO₂. Additionally, the Lewis acid sites in mixed SiO₂-TiO₂ composites [68] may also contribute to the enhanced performance of our Ru catalysts. Indeed, Kumar et al. [69,70], found that Lewis acid sites were favorable to the conversion of
LA to GVL, while Brønsted acid sites, which are normally absent in the structure of calcined TiO₂-SiO₂ composites [71,72], were responsible for the GVL ring opening to valeric acid (VA). It is worth noting that all these factors are interlinked and a harmonization between them is necessary to achieve a high performance catalyst for selective hydrogenation of LA to GVL. The more adequate electronic and crystal properties of the semi-conductor may also be favorable to the improvement of metal support interactions and the stability of the catalyst in water, both of which are likely to contribute to the superior activity of Ru@TiO₂-SiO₂ [31].

Recovery and recycling of the catalyst is an important challenge for industrial applications, especially when corrosive reactants such as LA are used, which may cause metal leaching and deactivation of the catalyst. Although Ru/C has proved to be one of the most active catalysts in the aqueous phase hydrogenation of LA, Al-Shaal et al. [21] have noticed a rapid deactivation during the recycling process. As illustrated in Figure 9, our best catalyst Ru@TiO₂-SiO₂ 3:3-ns was very stable in this reaction and could be reused in at least five consecutive catalytic runs without significant loss of catalytic performance. Its robustness can be ascribed to the combined effect of uniform and stable dispersion of Ru nanocrystals in a pore-confined space and their enhanced interactions with the TiO₂-SiO₂ support, as revealed by N₂-adsorption, HR-TEM, HAADF-STEM, and TPR.

<figure><img src="image_13.png" /><figcaption>**Figure 9.** Reusability tests on the Ru@TiO₂-SiO₂ 3:3-ns catalyst. Reaction conditions: 0.66 g LA (5.68 mmol), 77.6 mg supported catalyst (0.019 mmol Ru), 50 bar H₂, 20 mL H₂O, temperature 323 K, and reaction time 20 min.</figcaption></figure>

**3. Materials and Methods**

**3.1. Chemicals**

Randomly methylated β-cyclodextrin (denoted RaMeβCD, average degree of mo-
lar substitution (DS) 1.8 and average molar weight (Mw) 1310 g mol⁻¹) was a gift from
Wacker Chemie GmbH. Pluronic F127 with a chemical formula PEO₁₀₆PPO₇₀PEO₁₀₆ (PEO
= poly(ethylene oxide) and PPO = poly(propylene oxide)) (Mw 12,600 g mol⁻¹), titanium
isopropoxyde (Ti(OiPr)₄) (Mw 284.3 g mol⁻¹, d 0.96 g cm⁻³), tetraethylorthosilicate (TEOS)
(Mw 208.33 g mol⁻¹, d 0.93 g cm⁻³), nitric acid (HNO₃, 68%), levulinic acid (LA) (Mw
116.11 g mol⁻¹), and 4-hydroxypentanoic acid (4-HPA) (Mw 118.13 g mol⁻¹) were pur-
chased from Sigma Aldrich. Ruthenium (III) nitrosyl nitrate (Ru(NO)(NO₃)₃) (1.5% Ru,
Mw 318.10 g mol⁻¹) was procured from STREM Chemicals. All chemicals were used as
received without further purification.

3.2. *Preparation of Mesoporous TiO₂ and SiO₂-TiO₂ Materials*

The titanium dioxide (TiO₂) hydrosol was synthesized according to a previously re-
ported sol-gel method [73]. Briefly, to a mixture of 30 mL (0.1 mol) Ti(O'Pr)₄ and 27 mL
(0.35 mol) isopropanol, 160 mL of hot distilled water was added rapidly at 85 °C under
vigorous stirring (hydrolysis ratio h = H₂O/Ti = 88). After 15 min, 1.3 mL of nitric acid (HNO₃/Ti = 0.2) was added dropwise to peptize the viscous precipitate and the mixture was maintained under reflux at 85 °C for 16 h. A stable translucent suspension of TiO₂ nanoparticles (pH 2.1) crystallized in anatase (~70%) and brookite (~30%) was recovered at the end of the synthesis. The titanium concentration in the sol was 0.48 mol L⁻¹, as determined by weight loss on ignition at 1000 °C for 2 h. For the preparation of nanostructured TiO₂, Pluronic F127 (10 wt.%, F127/Ti molar ratio = 0.0165) and RaMeβCD (50 mg mL⁻¹, RaMeβCD/Ti molar ratio = 0.079) were added successively to 100 mL of the above titania sol. The mixture was stirred at room temperature for 3 h, and then allowed to equilibrate for 24 h. A nanostructured porous titania-denoted TiO₂-ns was obtained after drying the sol at 60 °C for 72 h, followed by rinsing with ethanol and further calcination at 500 °C for 2 h using a heating ramp of 5 °C min⁻¹. For the preparation of nanostructured TiO₂-SiO₂ composites, 0.648 g TEOS (Ti/Si molar ratio = 3) was added to 20 mL of the hybrid RaMeβCD-F127@TiO₂ suspension and maintained under stirring at room temperature for 1 h. Subsequently, the mixture was placed in an autoclave for hydrothermal treatment at 150 °C for 48 h. The recovered gel was placed in a Soxhlet extractor and rinsed with HCl (4%)-ethanol solution to remove the organic template. Finally, the solid was dried at 100 °C for 16 h, then calcined in air at 500 °C for additional 2 h. This sample was denoted TiO₂@SiO₂ 3:1-ns. TiO₂@SiO₂ 3:2-ns and TiO₂@SiO₂ 3:3-ns were prepared under the same conditions using 1.297 g and 1.945 g TEOS, respectively. In some experiments, template-free sol-gel titania (TiO₂-sg) and titanosilicate (TiO₂-SiO₂-sg) were also prepared for comparison.

### 3.3. Preparation of RuO₂@TiO₂ and RuO₂@TiO₂-SiO₂ Catalysts

Supported catalysts were prepared by an impregnation method using Ru(NO)(NO₃)₃ as precursor of RuO₂ because it was previously shown to provide the best results in terms of turn-over frequencies [26]. Typically, 800 mg of calcined TiO₂ or TiO₂-SiO₂ material were impregnated with 6 mL of an aqueous solution of Ru(NO)(NO₃)₃ (0.033 mol L⁻¹ Ru). The suspension was maintained under stirring at 75 °C until the water was completely evaporated. Then, this solid was calcined at 400 °C for 4 h under air flow. The resulting catalysts were denoted Ru@TiO₂-ns(sg) or Ru@TiO₂-SiO₂-x:y-ns(sg), where x:y indicates the Ti/Si molar ratio, whereas ns and sg refer to nanostructured and sol-gel catalysts, respectively.

### 3.4. Characterization Methods

Dynamic light scattering (DLS) measurements were performed at 25 °C with a Malvern Zeta Nanosizer instrument equipped with a 4 mW He-Ne laser operating at 633 nm using a backscattering detection system. The scattering angle θ was 173°. Powder X-ray diffraction patterns were acquired using a Siemens D5000 X-ray diffractometer in a Bragg-Brentano configuration with a Cu Kα radiation source. Scans were run over the angular 10° < 2θ < 80° domain with a step size of 0.02° and a step time of 2 s. Crystalline phases were identified based on the JCPDS database. FullProf software [74] and its graphical interface WinPlotr [75] were used for the refinement of the diffractograms. Profile matching refinement was used to determine the unit cell parameters of TiO₂, background, peak shape, and zero shift. The quality of the fit was determined visually by inspection of the difference plot and statistically by the goodness of fit (χ²), defined by:

$$ \chi^2 = \sum w_i (y_{io} - y_{ic})^2 / (N - P) \quad (1) $$

where wᵢ is the weight assigned to each observation; yᵢ₀ and yᵢₘ are the observed and calculated intensities, respectively, at the ith step; N is the number of points used in the refinement; and P is the number of least-squares parameters refined. The refinement was considered satisfactory when χ² was less than 3. Typical results obtained from profile matching on anatase/brookite and anatase/brookite/rutile mixtures are shown in Figure S12 (ESI). The average size (D) of the TiO₂ crystallites was then determined using
the Scherrer formula [76], $D = Kλ/(β \cos θ)$, where K is the shape factor (a value of 0.9 was taken in this study assuming that particles are spherical), λ is the X-ray radiation wavelength (1.54056 Å for Cu Kα), β is the full width at half-maximum (fwhm), and θ is the Bragg angle. The average size of the $RuO_2$ crystallites was estimated from the line broadening of the (110) reflection. $N_2$ adsorption-desorption isotherms were collected at -196 °C using an adsorption analyzer, Micromeritics Tristar 3020. Prior to analysis, 100-150 mg samples were outgassed at 260 °C overnight to remove the species adsorbed on the surface. From $N_2$ adsorption isotherms, specific surface areas were evaluated by the Brunauer-Emmett-Teller (BET) method [77] and pore size distributions were determined using the Barrett, Joyner, and Halenda (BJH) method assuming a cylindrical pore structure. Relative errors were estimated to be 5% for the surface area, 5% for the pore volume, and 20% for the BJH pore diameter. Temperature programmed reduction (TPR) measurements were carried out on a Micromeritics AutoChem 2920 chemisorption analyzer equipped with a thermal conductivity detector (TCD) used to monitor the $H_2$ consumption. Prior to analysis, 30-40 mg samples were placed in a U-tube quartz reactor and outgassed under argon flow at 120 °C for 2 h. After cooling to 25 °C, samples were reheated between 30 °C and 400 °C in a 5% $H_2$/Ar ($v/v$) flow with a flow rate of 10 mL min⁻¹ and a heating rate of 10 °C min⁻¹. Transmission electron microscopy (TEM), high-resolution TEM (HR-TEM), high-angle annular dark-field and bright-field scanning TEM (HAADF- and HAADF-STEM, respectively) images, and energy dispersive X-ray spectrometry (EDS) elemental mapping results were recorded on a MET FEI TITAN Themis 300 microscope with an accelerating voltage of 300 kV. The resolution of the STEM was less than 70 nm. The instrument is equipped with a Super-X EDX detector system with superior sensitivity and a fast EDS mapping. Four silicon drift detectors (SDDs) are integrated in the objective lens (S-TWIN). Images were recorded in STEM-HAADF and in annular bright-field (ABF) mode. The contrast in HAADF is proportional to the atomic number of the element. Therefore, in our catalysts Ru produces the brightest contrast. Relative content of Ti and Si in the mixed oxides was determined with the use of an energy dispersive micro-X-Ray fluorescence (XRF) spectrometer M4 TORNADO (Bruker) equipped with 2 anodes: a rhodium X-ray tube 50 kV/600 mA (30 W) and a tungsten X-Ray tube 50 kV/700 mA (35 W). For sample characterization, the X-rays Rhodium with a polycapillary lens enabling the excitation of an area of 200 µm was used. The detector was a silicon drift detector Si(Li) with <145 eV resolution at 100,000 cps (Mn Kα) working with a Peltier cooling (253°K). The measurement was done under vacuum (20 mbar). Quantitative analysis was performed using fundamental parameter (FP) (standardless). For each sample 36 points (of 200 µm) were analyzed.

### 3.5. Catalytic Tests

The catalytic performance of the supported catalysts was evaluated in the aqueous phase hydrogenation of LA to GVL. Prior to catalytic testing, the $RuO_2$-based composite was placed in a U-tube quartz reactor and reduced at 400 °C for 2 h under $H_2$ atmosphere (5% $H_2$/Ar) with a heating rate of 2 °C min⁻¹ and a flow rate of 10 mL min⁻¹. Reaction was performed according to previously reported conditions for water by Michel et al. [13] with some modifications. In a typical experiment, a 50 mL stainless steel batch autoclave reactor, equipped with a magnetic drive stirring and a thermostatic bath for the temperature control, was loaded with 660 mg LA (5.68 mmol), 77.6 mg de-supported catalyst (substrate/metal molar ratio = 300), and 20 mL ultra-pure water. The mixture was purged three times with nitrogen at room temperature, then heated at 50 °C and charged with $H_2$ to 50 bar. Reactions were run at a constant temperature of 50 °C for a certain reaction time (20 to 60 min) using a stirring speed of 750 rpm. At the end of the reaction, the reactor was cooled with cold water and the separation of the solid catalyst from the reaction mixture was performed through centrifugation and filtration. The composition of the reaction mixture was determined quantitatively by gas chromatography (GC). 50 µL of the separated liquid reaction products were diluted in 1 mL of chloroform in a GC vial. Benzaldehyde (1 wt.%)
was used as an internal standard. Products were analyzed using a Shimadzu GC-17A gas chromatograph (GC) equipped with a UBFFAP302525 column (30 m × 0.25 mm × 0.25 µm) and a flame ionization detector (FID). The FID and injection port temperatures were 250 °C. LA conversion and GVL yield were determined based on the calibration curves (see Figure S13, ESI) using the following equations:

$$ \text{Conversion (\%)} = \frac{\text{moles of LA reacted}}{\text{total moles of LA}} \times 100 \qquad (2) $$

$$ \text{Yield (\%)} = \frac{\text{moles of GVL formed}}{\text{total moles of LA}} \times 100 \qquad (3) $$

Nuclear magnetic resonance (NMR) spectra were recorded at 298 K on a Bruker Avance III HD 300 NanoBay spectrometer equipped with a 5 mm broadband probe BBFO with Z-gradients, operating at 7.05 T field strength (300 MHz). ¹H NMR chemical shifts are reported in ppm (δ) downfield from tetramethylsilane (TMS, in CDCl₃). ¹H NMR proved to be the most reliable method for the analysis of the intermediate product, 4-hydroxypentanoic acid (4-HPA), which is difficult to determine by GC. Typical profiles of the ¹H NMR spectra of the isolated products and the reaction mixture are shown in Figures S9 and S10, ESI.

For the recyclability tests, the solid was recovered by centrifugation, washed with water (10 mL), and then with chloroform (2–10 mL). GC analysis of the washing organic phase was performed to check the absence of any organic compounds from the catalytic reaction. The solid was dried overnight under vacuum to remove chloroform before starting the next run.

## 4. Conclusions

In summary, a versatile template-directed colloidal approach for the fabrication of composition-tuned TiO₂-SiO₂ materials with controllable pore sizes and crystal phase compositions has been established by constructing a RaMeβCD-Pluronic F127-titanium dioxide-silica mesophase before template removal. The supramolecular template together with the silica network were found to affect not only the structural and textural characteristics of the support but also the morphology of RuO₂ nanostructures which underwent shape transformation from spherical to plate-like, lozenge-like, and rod-like particles. When utilized as catalysts, Ru particles supported on mesoporous TiO₂-SiO₂ mixed oxides globally displayed higher catalytic activity in the hydrogenation of levulinic acid (LA) to γ-valerolactone (GVL) compared to Ru deposited on mesoporous TiO₂. The enhanced catalytic performance was attributed to the larger surface area and higher porosity of TiO₂-SiO₂ support, which promoted uniform dispersion of Ru nanoparticles, reducing particle agglomeration and mass transfer limitations during the catalytic process. Moreover, the activity was improved by using elongated Ru structures as opposed to spherical Ru particles. Thus, a 100% conversion of LA together with a 99% yield in GVL was achieved at 50 °C under 50 bar H₂ in one hour on a Ru@TiO₂-SiO₂ 3:3-ns catalyst in the presence of water. Importantly, this catalyst demonstrated high stability in this reaction and could be reused at least five times without an obvious loss of activity. Its robustness was ascribed to the confinement effects of nanocrystals in a highly porous TiO₂-SiO₂ matrix, as well as the strong metal support interactions. Altogether, this work successfully proves the important role of RaMeβCD-based supramolecular assemblies in the fabrication of composition-tuned heterogeneous catalysts with enhanced catalytic performance in aqueous phase hydrogenation reactions.

**Supplementary Materials:** The following are available online at https://www.mdpi.com/1422-0067/22/4/1721/s1, Figure S1: DLS plots of micellar solutions prepared with 3% *w/v* F127 (A), 5% *w/v* F127 (B) and 15% *w/v* F127 (C) and increasing concentrations of RaMeβCD from 10 mg mL⁻¹ to 110 mg mL⁻¹, Figure S2: N2-adsorption isotherms and corresponding pore size distributions (inset) of SiO₂-sg and SiO₂-ns, Figure S3: XRD patterns of TiO₂-SiO₂ 3:3-sg (a) and RuO₂@TiO₂-SiO₂
3:3-sg (b), Figure S4: HAADF-STEM image (a) and corresponding EDX elemental mapping of Ti (b), Si (c), Ru (d) and O (e) of RuO₂@TiO₂-SiO₂ 3:1-ns catalyst, Figure S5: Representative HR-TEM images of RuO₂@TiO₂-SiO₂ 3:1-ns catalyst, Figure S6: Representative HAADF-STEM images of RuO₂@TiO₂-SiO₂ 3:2-ns catalyst showing formation of rod-shaped crystals of 50–100 nm length and 20–40 nm width together with corresponding EDX elemental mapping of Ti (e), Si (f), Ru (g) and O (h), Figure S7: HAABF- (a) and HAADF-STEM (b) images and corresponding EDX elemental mapping of Ti (c), Si (d), Ru (e) and O (f) (B) of RuO₂@TiO₂-SiO₂ 3:3-ns catalyst, Figure S8: TPR patterns of RuO₂@TiO₂-SiO₂ 3:3-sg (a) and RuO₂@TiO₂-SiO₂ 3:3-ns (b), Figure S9: ¹H NMR (300MHz, CDCl₃) spectra of (A) LA and (B) GVL, Figure S10: ¹H NMR (300MHz, CDCl₃) spectrum of reaction mixture in the aqueous phase hydrogenation of LA to GVL showing formation of 4-hydroxypentanoic acid (4-HPA) as intermediate, Figure S11: Comparison of LA conversions and GVL yields obtained with Ru catalysts supported on different mixed oxides prepared without template, Figure S12: Observed (red scatter) and calculated (black line) XRD patterns resulting from pattern matching of TiO₂-sg (A) and TiO₂-SiO₂ 3:3-ns (B), Figure S13. Calibration curves of LA (A) and GVL (B) determined by GC using benzaldehyde as internal standard, Table S1: Textural characteristics of SiO₂-sg and SiO₂-ns supports after calcination at 500 °C, Table S2: Textural characteristics of sol-gel and nanostructured Al₂O₃ and Al₂O₃-based mixed oxides after calcination at 500 °C.

**Author Contributions:** The manuscript was written through contributions of all authors. R.B. supervised the project and wrote the paper. C.D. synthesized Ru-based catalysts and carried out DLS, N₂-adsorption, and TPR measurements. C.D. and S.N. performed the catalytic tests. A.A. acquired HR-TEM and HAADF-STEM images as well as EDS elemental mapping. A.P. and E.M. contributed in the reviewing and editing of the manuscript. All authors discussed the results and commented on the manuscript. All authors have read and agreed to the published version of the manuscript.

**Funding:** The TEM facility in Lille is supported by the Conseil Régional des Hauts-de-France and the European Regional Development Fund (ERDF).

**Institutional Review Board Statement:** Not applicable.

**Informed Consent Statement:** Not applicable.

**Data Availability Statement:** The data presented in this study are available in article and supplementary material.

**Acknowledgments:** We are grateful to Jérémy Kernel (Univ. Artois) and Laurence Burylo (Univ. Lille) for technical assistance with NMR and XRD respectively, as well as to Joëlle Thuriot (Univ. Lille) for help with XRF analysis.

**Conflicts of Interest:** The authors declare no conflict of interest. The funders had no role in the design of the study; in the collection, analyses, or interpretation of data; in the writing of the manuscript; or in the decision to publish the results.

**Abbreviations**

<table><tr><td>CD</td><td>Cyclodextrin</td></tr><tr><td>RaMeβCD</td><td>Randomly methylated β-cyclodextrin</td></tr><tr><td>GVL</td><td>γ-valerolactone</td></tr><tr><td>4-HPA</td><td>4-hydroxypentanoic acid</td></tr><tr><td>LA</td><td>Levulinic acid</td></tr><tr><td>TEOS</td><td>Tetraethyl orthosilicate</td></tr><tr><td>Ti(O<sup>1</sup>Pr)<sub>4</sub></td><td>Titanium isopropoxyde</td></tr><tr><td>DLS</td><td>Dynamic light scattering</td></tr><tr><td>JCPDS</td><td>Joint committee on powder diffraction standards</td></tr><tr><td>XRD</td><td>X-ray diffraction</td></tr><tr><td>S<sub>BET</sub></td><td>Surface area determined by the Brunauer, Emmett, and Teller method</td></tr><tr><td>BJH</td><td>Barrett, Joyner, and Halenda</td></tr><tr><td>TPR</td><td>Temperature programmed reduction</td></tr><tr><td>XRF</td><td>X-ray fluorescence</td></tr><tr><td>HR-TEM</td><td>High-resolution transmission electron microscopy</td></tr><tr><td>HAABF-STEM</td><td>High-angle annular bright-field scanning TEM</td></tr></table>
<table><tr><td>HAADF-STEM</td><td>High-angle annular dark-field scanning TEM</td></tr><tr><td>EDS</td><td>Energy dispersive X-ray spectrometry</td></tr><tr><td>ICP-OES</td><td>Inductive coupled plasma optical emission spectroscopy</td></tr><tr><td>NMR</td><td>Nuclear magnetic resonance</td></tr><tr><td>GC</td><td>Gas chromatography</td></tr></table>

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