Guided Crystallization of Zeolite Beads Composed of ZSM-12 Nanosponges

The direct route using a bifunctional amphiphilic structuring agent for the synthesis of hierarchical nanozeolites coupled with pseudomorphic transformation was used for the crystallization of hierarchized zeolite beads/hollow spheres composed of ZSM-12 (MTW structural-type) with nanosponge morphology. These beads/hollow spheres have the same average diameter of 20 μm as their counterpart amorphous mesoporous silica beads used as precursor in the starting synthesis mixture. The effects of synthesis parameters, such as stirring and treatment time at 140 ◦C, on the morphology, structure, and texture of the materials have been investigated using X-ray diffraction (XRD), N2 sorption, scanning electronic microscopy (SEM), and transmission electronic microscopy (TEM) techniques. Static conditions were found necessary to maintain the morphology of the starting amorphous silica beads. An Ostwald ripening phenomenon was observed with the increase in hydrothermal treatment time leading to the dissolution of the interior of some beads to form core shell beads or hollow spheres with larger crystals on the outer surface. These ZSM-12 beads/hollow spheres possess higher porous volume than conventional ZSM-12 zeolite powder and can be used directly for industrial applications.


Introduction
Zeolites constitute a category of aluminosilicate crystals with microporous frameworks. They are good candidates for adsorption, catalysis and separation due to their shape selectivity and high thermal stability [1][2][3][4][5][6]. However, the diffusion of molecules is limited in micropores and thus the performance of zeolites in catalytic reactions or adsorption often depends strongly on the size, morphology and porosity (pore size and pore topology) of the crystals [7][8][9][10]. In catalysis, diffusional limitations often lead to coke formation or reduce the accessibility to active sites. For molecular decontamination, adsorption capacity and kinetics are mainly governed by pore size and porous volume. Zeolites having a one-dimensional (1D) pore system, such as MTW, TON, or MOR type, and generally suffer from a long diffusion path in crystals with high aspect ratios (length/width) and pore channels oriented along the length [11]. In recent years, a particular attention has been brought to rationally design the crystal morphology and/or the porosity of a given zeolite in order to reduce diffusion path in microporosity [12]. In this context, the reduction of crystal size or introducing larger pores appeared the best strategies. Post-treatments consisting in dealumination or desilication are the conventional methods for generating mesopores within zeolite crystals [13][14][15][16]. The crystallization of zeolites with hierarchical micro/mesoporous structures by using bifunctional amphiphilic structure directing agent was also identified as a performant alternative [9,[17][18][19][20][21][22][23][24][25][26]. Moreover, the addition of additives, such as crystal growth modifiers [27][28][29] or seed crystals (salt-aided seed-induced route) [8,30], also makes it possible to tailor the size and the morphology of the crystals by inhibiting the crystal growth along certain specific network planes or by controlling the process of dissolution-recrystallization, respectively.
ZSM-12 zeolite of MTW-type is a highly silicic 1D-pore system with a framework Si/Al molar ratio always higher than 20, and has shown interesting features for acid catalysis such as high coking resistance and high chemical stability [31]. It was first synthesized by Rosinski and Rubin [32] in a reaction medium containing diethyl sulphate and triethylamine. In 1985, LaPierre et al. resolved the structure using X-ray powder diffraction [33]. The unit cell is monoclinic, the space group is C2/m and the unit cell parameters are: a = 24.88, b = 5.02 Å, c = 12.15 Å, and β = 107.7 • . The structure contains rings with four, five, and six T atoms (T = Si or Al) and has a one-dimensional system of channels with 12 T atoms with pore openings of~5.6 × 6.1 Å. Looking at the structure in a direction perpendicular to the axis of the channels we can observe that the walls are formed only by six-atom rings T with an opening of about 2.5 Å. This small opening prevents the passage of adsorbed molecules between the channels [34]. As a consequence, ZSM-12 zeolite is characterized by non-interconnecting tubular-like linear channels that were identified to be responsible for not allowing the accumulation of coking precursors [31].
The particular micropores dimensions of the ZSM-12 zeolite, make it performant catalyst in reactions involving cyclic hydrocarbons. Pazzucconi et al. used ZSM-12 zeolite for alkylation of naphthalene in liquid phase at high pressure in the presence of 1,2,4-trimethylbenzene as a solvent, and they reported a high activity and high selectivity of ZSM-12 zeolite to 2,6-dimethylnaphthalene [35,36]. Higher stability and higher activity on the reaction time in the catalytic cracking of naphthalene were observed on ZSM-12 zeolite, which can provide insight into the catalytic performance for many reactions. However, ZSM-12 zeolite also suffers diffusional limitations in micropores and the hierarchization of the pore network was investigated and revealed beneficial to improve its catalytic performance.
Dugkhuntod et al. recently reported the synthesis of hierarchical ZSM-12 nanolayers via a dual template method [37]. Hierarchical ZSM-12 nanolayers exhibit an improvement of catalytic activity in terms of levulinic acid conversion compared to other hierarchical zeolite nanosheets, such as MFI (ZSM-5) and FAU. The better catalytic performance was related to the enhanced mesoporosity and the presence of a large one-dimensional 12-membered ring network, which can promote the accessibility of bulky-molecules to active sites of zeolite.
Zeolites or hierarchized zeolites synthesized with conventional hydrothermal routes leads to micrometer-sized crystals or nanocrystal aggregates, respectively, forming fine powder products. However, the use of these materials in powder form can be disadvantageous for certain industrial applications such as those based on continuous flow processes. Indeed, they can generate too much pressure drop and cause clogging of the cartridges/columns/filters used on an industrial scale. Moreover, these zeolite powders can be a source of secondary contamination and often fine powders causes problems of handling (due to particles spreading). Therefore, the development of methods for shaping these materials into objects of controllable shape and size is of great technological importance. However, shaping methods of zeolite powder usually require several steps such as compacting, grinding and sieving for obtaining grains of similar size, or assembling the zeolite particles by extrusion or mixing in presence of organic (e.g., polymers) or inorganic (e.g., clays, sodium silicate) binders, which can reduce the performance of the zeolite materials [38][39][40], or removal of sacrificial macrotemplates (resin, . . . ) [41,42]. A one-step and binderless process such as pseudomorphic transformation is an interesting alternative for shaping zeolite powder. This strategy consists by controlling the dissolution/crystallization process to transform a shaped material into another one having different chemical composition but the same shape. This concept was successfully used by Anne Galarneau's team to synthesize micrometric beads and zeolite monoliths of the LTA, SOD and FAU type with low Si/Al ratios [43][44][45][46]. Our group has recently reported the direct synthesis of hierarchical ZSM-5 beads [47] and monoliths with nanosheets morphology [48], and also plain and hollow purely silica beads of silicalite-1 nanosheets by using the pseudomorphic transformation method [49]. Here, we report the use of the pseudomorphic transformation concept to elaborate hierarchical ZSM-12 zeolite beads with nanosponges morphology thanks to the use of a dual-porogenic surfactant as a template and growth inhibitor, which was used for zeolite *BEA nanosponge synthesis [9,21,25]. This surfactant has been synthetized in three steps following the procedure described by Na et al. [21]. 16.2 g (0.01 mol) of 1-bromodocosane (TCI EUROPE N.V., Zwijndrecht, Belgium) and 68.8 g (0.1 mol) of N,N,N',N'-tetramethyl-1,6-diaminohexane (Sigma-Aldrich Chemie S.a.r.l., Saint-Quentin Fallavier, France) were dissolved in 400 mL of acetonitrile/toluene mixture (1:1 vol/vol) and heated under reflux at 70 • C for 12 h with magnetic stirring. After cooling to room temperature, the solvent was evaporated by rotary evaporator, and the product was filtered, washed with diethyl ether, and dried under vacuum at 50 • C. The product obtained was denoted C 22-6-0 .
Purity was checked by 1 H liquid nuclear magnetic resonance (NMR), the chemical shifts obtained are as follows: 1

Synthesis of ZSM-12 Nanosponges Beads
First, 0.3 g of sodium hydroxide (NaOH 99%, Carlo Erba Reagents, Val-de-Reuil, France) and 0.037 g sodium aluminate (NaAlO 2 92%, Strem Chemicals, Inc., Bischeim, France) were dissolved in 21.3 g of distilled water. Then, 6.14 g of pure ethanol (ETOH, 99%, VWR International S.A.S, Fontenay-sous-Bois, France) and 1.6 g of the dual-porogenic surfactant the N6-Diphe were added to the previous mixture. In a next step, the obtained mixture was mixed with 1 g of amorphous mesoporous silica beads with an average size of 20 µm (data given by the supplier SiliCycle Inc., Quebec, Canada) to set the molar composition to: 1 SiO 2 : 0. 22  The synthesized samples are denoted t-S, or t-NS, where "t" stands for the hydrothermal treatment time at 140 • C, and "S" or "NS" means that the samples was synthetized under tumbling stirring or not (static mode), respectively

Characterization of Zeolite Beads
The purity and crystallinity of the obtained samples was checked by X-ray diffraction (XRD). The samples were introduced in glass capillaries and the X-ray patterns were recorded using a STOE STADI-P (STOE & Cie GmbH, Darmstadt, Germany) diffractometer using Cu Kα 1 radiation (λ = 0.15406 nm) in the range 3 • < 2θ < 50 • .
Scanning and transmission electron microscopy (SEM and TEM) were performed to analyze morphology, homogeneity, and particle sizes. Philips XL30 FEG (Field Emission Gun) (Philips, Verdun, France) and JEOL JSM-7900F (JEOL, Val-de-Reuil, France) scanning electron microscopes (SEM) were used. The later was equipped with a BRUKER QUANTAX spectrometer (BRUKER, Champs sur Marne, France) for the energy dispersive X-ray analyses (EDX). The transmission electron microscopy (TEM) was carried out on a JEOL (Val-de-Reuil, France) model ARM 200, operating at 200 kV, with a point-to point resolution of 80 pm. For EDX analyses, samples were previously embedded in an epoxy resin for cold mounting (Epofix from Struer S.A.S. Champigny sur Marne, France), which was grinded with various grinding papers and then polished until a soft surface was obtained.
Nitrogen sorption isotherms were recorded at −196 • C using a Micromeritics (Merignac, France) sorptometer (model ASAP 2420). In prior analyses, the samples were out-gassed under vacuum at 300 • C for 15 h. The BET method was used for determining the specific surface area. The total pore volume was determined from the total amount of N 2 adsorbed at saturation (i.e., at p/p • = 0.99 in absence of textural porosity). The Density Functional Method (DFT) method was applied on the adsorption branch in order to obtain the pore size distributions [50]. The microporous volumes were calculated by using a modified t-plot method.
The amounts of dual porogenic agent occluded within the porosity of sample were determined by thermogravimetric analysis (METTLER TOLEDO, Viroflay, France, model TG/DSC STARe) from 20 to 800 • C under air with a heating rate of 5 • C/min −1 .
The Si/Al molar ratios were determined using X-ray fluorescence spectrometry (XRF) performed on a PANalytical (Limeil-Brévannes, France) equipment model Zetium and from EDX analyses.

Results and Discussion
The purity and crystallinity of the synthesized zeolites were investigated by X-ray diffraction ( Figure 1). The X-ray patterns of the all obtained materials present diffraction peaks, which correspond to a pure phase of ZSM-12 zeolite in agreement with the corresponding patterns available in the literature [51]. The diffraction peaks are broader for samples hydrothermally treated under static conditions for 4, 5 and 7 days (4-NS, 5-NS and 7-NS, respectively), which indicate a small crystal size and/or a low crystallinity degree. The thinner diffraction peaks with higher intensity observed after 4 days of hydrothermal treatment with mechanical stirring (4-S) and after 14 and 21 days in static mode (14-NS and 21-NS, respectively) indicate the presence of larger crystal sizes and/or high crystallinity degree. SEM images displayed in Figure 2 show that the morphology of the parent silica beads ( Figure  S1) has been totally lost for the sample 4-S synthesized under stirring ( Figure 2a). However, the nanosponge morphology was observed by TEM ( Figure 3a). Indeed, TEM image show nano-sized zeolite crystals delimiting mesopores with narrow pore size distribution as a result of the selfassembly of the long hydrocarbon chains of the multiammonium surfactant used as structure directing agent. This, in complement of XRD data, indicates that stirring favor a fast crystallization of ZSM-12 nanosponges but induce the loss of the parent bead morphology. On the other hand, the spherical morphology of the parent amorphous silica beads was maintained when the hydrothermal treatment was carried out in static mode for all investigated durations (Figure 2b-f). The breaking of the beads upon stirring allowed a faster diffusion of reactants present in the liquid phase (aluminum source, bifunctional structuring agent N6-Diphe) to the silica backbone compared to the plain beads. SEM images at high magnification displayed in Figure 2 show that beads are constituted of spherical agglomerates of ZSM-12 nanocrystals, with an average of 400 ± 90 nm diameter after four and five days of hydrothermal treatment. The size of the agglomerates of ZSM-12 nanocrystals seems to increase slightly to reach about 1 ± 0.2 µm by increasing the duration of the hydrothermal treatment to seven and 14 days, and reaches about 1.7 ± 0.2 µm after 21 days. In parallel, the size ZSM-12 nanocrystals composing these agglomerates increases from 4 nm (4-S and 4-NS samples) to reach a maximum of 80 nm after 21 days of hydrothermal treatment as shown in Figure 3a,b. The nanocrystal size distribution seems also to increase while increase the hydrothermal treatment time, especially for 7-NS, 14-NS and 21-NS samples (Figure 3c-e). These results are consistent with the sharper X-ray diffractions peaks when increasing the time of the hydrothermal treatment. According to the TEM images of samples 4-S, 4-NS, 7-NS, 14-NS, and 21-NS displayed in Figure 3, nanosponges are composed by randomly agglomerated nanocrystals interconnected by mesopores, which are characteristic of nanosponge morphology [9,25]. Since beads have been crushed for TEM observations, it is difficult to identify the location of the crystals of different sizes in the obtained beads. However, by correlation with SEM observations these big crystals are probably located at the outer surface of the beads while small ones are inside as already observed in our previous work on the synthesis of silicalite-1 zeolite beads and hollow spheres, where the crystallization seems to begin on the external surface of the beads and to diffuse with the time inside the beads [49]. SEM images displayed in Figure 2 show that the morphology of the parent silica beads ( Figure S1) has been totally lost for the sample 4-S synthesized under stirring (Figure 2a). However, the nanosponge morphology was observed by TEM ( Figure 3a). Indeed, TEM image show nano-sized zeolite crystals delimiting mesopores with narrow pore size distribution as a result of the self-assembly of the long hydrocarbon chains of the multiammonium surfactant used as structure directing agent. This, in complement of XRD data, indicates that stirring favor a fast crystallization of ZSM-12 nanosponges but induce the loss of the parent bead morphology. On the other hand, the spherical morphology of the parent amorphous silica beads was maintained when the hydrothermal treatment was carried out in static mode for all investigated durations (Figure 2b-f). The breaking of the beads upon stirring allowed a faster diffusion of reactants present in the liquid phase (aluminum source, bifunctional structuring agent N 6 -Diphe) to the silica backbone compared to the plain beads. SEM images at high magnification displayed in Figure 2 show that beads are constituted of spherical agglomerates of ZSM-12 nanocrystals, with an average of 400 ± 90 nm diameter after four and five days of hydrothermal treatment. The size of the agglomerates of ZSM-12 nanocrystals seems to increase slightly to reach about 1 ± 0.2 µm by increasing the duration of the hydrothermal treatment to seven and 14 days, and reaches about 1.7 ± 0.2 µm after 21 days. In parallel, the size ZSM-12 nanocrystals composing these agglomerates increases from 4 nm (4-S and 4-NS samples) to reach a maximum of 80 nm after 21 days of hydrothermal treatment as shown in Figure 3a,b. The nanocrystal size distribution seems also to increase while increase the hydrothermal treatment time, especially for 7-NS, 14-NS and 21-NS samples (Figure 3c-e). These results are consistent with the sharper X-ray diffractions peaks when increasing the time of the hydrothermal treatment. According to the TEM images of samples 4-S, 4-NS, 7-NS, 14-NS, and 21-NS displayed in Figure 3, nanosponges are composed by randomly agglomerated nanocrystals interconnected by mesopores, which are characteristic of nanosponge morphology [9,25]. Since beads have been crushed for TEM observations, it is difficult to identify the location of the crystals of different sizes in the obtained beads. However, by correlation with SEM observations these big crystals are probably located at the outer surface of the beads while small ones are inside as already observed in our previous work on the synthesis of silicalite-1 zeolite beads and hollow spheres, where the crystallization seems to begin on the external surface of the beads and to diffuse with the time inside the beads [49].  The nitrogen adsorption-desorption isotherms at 77 K of the calcined materials are shown in Figure 4a. The nitrogen adsorption-desorption isotherm of the parent silica beads is of type IV (according to an IUPAC classification) ( Figure S2) [52]. For the samples obtained by pseudomorphic transformation, isotherms are a mixture of type I (low relative pressure p/p°) and type IV (high p/p°). The nitrogen adsorption-desorption isotherms at 77 K of the calcined materials are shown in Figure 4a. The nitrogen adsorption-desorption isotherm of the parent silica beads is of type IV (according to an IUPAC classification) ( Figure S2) [52]. For the samples obtained by pseudomorphic transformation, isotherms are a mixture of type I (low relative pressure p/p • ) and type IV (high p/p • ). All isotherms present a H3 hysteresis in the 0.4 < p/p 0 < 1 range, whichis characteristic of mesoporosity induced by the alkyl chains and the phenyl groups of the dual-porogenic surfactant (N6-Diphe). However, for 4-S and 4-NS samples, some interparticle mesoporosity is also clearly observed (type II at high p/p • ). The type I shape of the isotherms is coherent with the presence of the micropores. The textural properties of all materials determined from the nitrogen adsorption-desorption isotherms are presented in Table 1. The microporous volumes have been determined by the t-plot method with the correction proposed by Galarneau et al. for hierarchical zeolites [53,54]. The microporous volume of the sample 4-S, where the morphology of the starting beads is not conserved, is 0.19 cm 3 /g. A lower microporous volume (0.15 cm 3 /g) has been measured for the sample synthesized with the same duration (4 days) but under static conditions. These microporous volumes are higher than the one expected for conventional ZSM-12 zeolite (0.05-0.11 cm 3 /g) [37,55,56] because of the presence of secondary micropores with a diameter of 1.5 nm revealed by the pore size distribution obtained by applying DFT Method [50] (Figure 4b). The volume of these secondary micropores seem to decrease by increasing the hydrothermal treatment time. It is assumed that they were generated by the presence of dual-porogenic surfactant N6-Diphe. Indeed, such secondary microporosity generated by this kind of bifunctional amphiphilic structuring agent was already observed in hierarchized ZSM-5 [47]. It is noteworthy that secondary micropores of the same size are also present in the parent amorphous silica beads. However, no porosity was detected on as-made materials, suggesting that original secondary micropores (due to amorphous silica beads) disappeared upon pseudomorphic transformation. The total microporous volume decreases to about 0.11-0.13 cm 3 /g with the increase of the hydrothermal treatment time (5 days and more). This phenomenon can be explained by "Ostwald ripening" when small crystals are used as nutriment to give birth to bigger ones. This assumption is consistent with SEM and TEM observations, and with the thinner diffraction peaks obtained by XRD. Figure 4b shows the presence of mesopores of about 5 nm in average diameter with a wide mesopore size distribution going from 2 to 15 nm for the obtained samples. These mesopores do not come from the parent amorphous silica beads since these latter have also a large pore size distribution but centered at 10 nm ( Figure S1). They are formed by the micellization of the hydrophobic long chains of dual structure directing agents and are responsible of the nanosponge morphology. It is noteworthy that mesoporous volumes (without interparticle porosity for 4-NS sample) increase linearly with the hydrothermal treatment time ( Figure 5).      TGA analysis under air done on the as-synthesized samples shows 2 weight losses: a small one between 30 and 120 • C corresponding to the physisorbed water and a large one between 120 and 700 • C corresponding to the oxidation of the dual-porogenic surfactant used for the synthesis ( Table 1). As well as the mesoporous volume, the amount of dual-porogenic surfactant determined by TGA increases linearly with the hydrothermal treatment time ( Figure 6). This indicates that the incorporation of the dual porogenic surfactant N6-Diphe increases with the hydrothermal treatment time, resulting in a higher internal mesopore volume. In order to study the evolution of the inner part of the spheres and the silica and aluminum distribution as function of the hydrothermal treatment time, SEM observations and EDX analyses ( Figure 7) were performed on three of the synthesized samples. For that, it was necessary to prepare cross section of the beads by embedding the samples in resin and then polish them. After four days of hydrothermal treatment in static mode, beads are plain, and the distribution of silica and aluminum is homogeneous on the whole of the bead indicating the nanocrystals formation in the whole beads. When increasing the duration of treatment to seven days, core-shell beads are mainly observed with a more important silica content in the shell than in the core. Few hollow spheres are also observed indicating the partial dissolution of the bead center. After 21 days, core-shell beads are still observed in coexistence with a higher number of hollow spheres. These observations are consistent with the assumption that the crystallization begins from the outer surface and propagates to the center, and with time the interior of the beads dissolve to feed the growth of the crystals located at the surface of the shell. From EDX analyses performed on all ZSM-12 nanosponges beads and hollow spheres, an average value of 30 was determined for the Si/Al ratio, which is close to the average value of 35 determined by XRF. These values are coherent with the initial Si/Al molar ratio of the precursor gel that was 40. In order to study the evolution of the inner part of the spheres and the silica and aluminum distribution as function of the hydrothermal treatment time, SEM observations and EDX analyses ( Figure 7) were performed on three of the synthesized samples. For that, it was necessary to prepare cross section of the beads by embedding the samples in resin and then polish them. After four days of hydrothermal treatment in static mode, beads are plain, and the distribution of silica and aluminum is homogeneous on the whole of the bead indicating the nanocrystals formation in the whole beads. When increasing the duration of treatment to seven days, core-shell beads are mainly observed with a more important silica content in the shell than in the core. Few hollow spheres are also observed indicating the partial dissolution of the bead center. After 21 days, core-shell beads are still observed in coexistence with a higher number of hollow spheres. These observations are consistent with the assumption that the crystallization begins from the outer surface and propagates to the center, and with time the interior of the beads dissolve to feed the growth of the crystals located at the surface of the shell. From EDX analyses performed on all ZSM-12 nanosponges beads and hollow spheres, an average value of 30 was determined for the Si/Al ratio, which is close to the average value of 35 determined by XRF. These values are coherent with the initial Si/Al molar ratio of the precursor gel that was 40.

Conclusions
The pseudomorphic transformation pathway was applied for the synthesis of 20-µm beads composed of ZSM-12 zeolite nanosponges with MTW structure type. When hydrothermal treatment was performed with mechanical stirring (4-S), the starting amorphous silica spheres were broken and the diffusion of reactants within mesopores of the starting amorphous silica beads was faster. The crystallization of the amorphous silica walls into ZSM-12 was thus faster compared to the case when hydrothermal treatment was performed under static conditions for the same duration (4-NS). In both cases, ZSM-12 nanosponges were formed as observed by TEM images but the crystallization rate is lower for 4-NS, in agreement with broader XRD peaks for this latter sample. With one additional day of hydrothermal treatment under static conditions (5-NS), the crystallization rate increases in accordance with XRD data that showed thinner peaks. After seven days of hydrothermal treatment at 140 °C under static conditions an Ostwald ripening phenomenon has started, which results in growth of the crystals located at the outer surface of the beads. These bigger crystals are responsible for the thinner peaks observed by XRD. As observed by SEM and EDX, they form a shell rich in silicon. Beads and hollow spheres are composed of ZSM-12 zeolite nanocrystals (4 to 80 nm in size) interconnected to each other through a mesoporous network giving rise to a nanosponge morphology. This morphology generates an additional porosity (mesoporosity and secondary microporosity) to the microporosity of the zeolites (total pore volume greater than the one of conventional ZSM-12 zeolite) and improves the diffusion within this material, which should result in improving the kinetics as well as the adsorption capacities and catalytic properties of this material.

Conclusions
The pseudomorphic transformation pathway was applied for the synthesis of 20-µm beads composed of ZSM-12 zeolite nanosponges with MTW structure type. When hydrothermal treatment was performed with mechanical stirring (4-S), the starting amorphous silica spheres were broken and the diffusion of reactants within mesopores of the starting amorphous silica beads was faster. The crystallization of the amorphous silica walls into ZSM-12 was thus faster compared to the case when hydrothermal treatment was performed under static conditions for the same duration (4-NS). In both cases, ZSM-12 nanosponges were formed as observed by TEM images but the crystallization rate is lower for 4-NS, in agreement with broader XRD peaks for this latter sample. With one additional day of hydrothermal treatment under static conditions (5-NS), the crystallization rate increases in accordance with XRD data that showed thinner peaks. After seven days of hydrothermal treatment at 140 • C under static conditions an Ostwald ripening phenomenon has started, which results in growth of the crystals located at the outer surface of the beads. These bigger crystals are responsible for the thinner peaks observed by XRD. As observed by SEM and EDX, they form a shell rich in silicon. Beads and hollow spheres are composed of ZSM-12 zeolite nanocrystals (4 to 80 nm in size) interconnected to each other through a mesoporous network giving rise to a nanosponge morphology. This morphology generates an additional porosity (mesoporosity and secondary microporosity) to the microporosity of the zeolites (total pore volume greater than the one of conventional ZSM-12 zeolite) and improves the diffusion within this material, which should result in improving the kinetics as well as the adsorption capacities and catalytic properties of this material.

Supplementary Materials:
The following are available online at http://www.mdpi.com/2073-4352/10/9/828/s1, Figure S1. Scanning electron microscopy (SEM) images of the parent amorphous 20 µm silica spheres. An average size of 23 ± 3 µm was determined from measurements on about 100 beads, Figure S2. (a) Nitrogen sorption isotherm at 77 K and (b) DFT pore size distribution determined from the adsorption branch of the N 2 isotherm for the parent amorphous silica beads.