Molecular Bottom-Up Approaches for the Synthesis of Inorganic and Hybrid Nanostructures

Chemical routes for the synthesis of nanostructures are fundamental in nanoscience. Among the different strategies for the production of nanostructures, this article reviews the fundamentals of the bottom-up approaches, focusing on wet chemistry synthesis. It offers a general view on the synthesis of different inorganic and hybrid organic–inorganic nanostructures such as ceramics, metal, and semiconductor nanoparticles, mesoporous structures, and metal–organic frameworks. This review article is especially written for a wide audience demanding a text focused on the basic concepts and ideas of the synthesis of inorganic and hybrid nanostructures. It is styled for both early researchers who are starting to work on this topic and also non-specialist readers with a basic background on chemistry. Updated references and texts that provide a deeper discussion and describing the different synthesis strategies in detail are given, as well as a section on the current perspectives and possible future evolution.


Introduction
The design of chemical strategies for the nanostructuration of materials is one of the basic pillars for the development of both nanoscience and nanotechnology. The term nanostructure is used to refer to structures showing properties that are different to the ones shown in both the molecular and bulk solid state, and in which at least one of their dimensions or structural attributes are in an approximate size range from 1 to 100 nm [1], although this range can be somehow flexible. Some typical examples of properties shown by nanostructures, depending on their size and shape, are the luminescence in quantum [2][3][4] and carbon dots [5], the plasmonic properties in metal nanoparticles [6], and the room-temperature ferromagnetism exhibited by nanoparticles of intrinsically nonmagnetic inorganic materials [7]. Nanoscience is thus considered to be situated between atomic and molecular chemistry, and solid state and materials chemistry.
Nanostructures themselves are not advantageous or disadvantageous, when compared to other structures. They are just more appropriate for specific applications, which are connected to the size range between the atomic-molecular and the bulk scales. For example, most of the biomolecular interactions take place within the 1-100 nm size range [8,9]. For this reason, nanostructures are especially relevant in nanomedicine, with applications in imaging, diagnosis, and therapy, among others [10]. In fact, some drug formulations based graduate or undergraduate students, early researchers who start to work on the chemistry of nanosystems, as well as for non-specialist readers who require information on the basics and fundamentals of this experimental discipline. An updated collection of references is given, including more exhaustive and detailed articles in which the synthesis of inorganic and hybrid nanostructures is discussed in detail, being especially appropriate for readers who require a deeper description of this topic. Among them, we especially recommend a recent review by Hunh et al. [29], which covers and explains the synthesis of many different inorganic NPs in detail. A final section on the perspectives and the possible evolution within the synthesis of such nanosystems is also given.
Inorganics 2021, 9,58 3 of 24 vide a general view on the synthesis of inorganic and hybrid nanostructures, being especially suitable for graduate or undergraduate students, early researchers who start to work on the chemistry of nanosystems, as well as for non-specialist readers who require information on the basics and fundamentals of this experimental discipline. An updated collection of references is given, including more exhaustive and detailed articles in which the synthesis of inorganic and hybrid nanostructures is discussed in detail, being especially appropriate for readers who require a deeper description of this topic. Among them, we especially recommend a recent review by Hunh et al. [29], which covers and explains the synthesis of many different inorganic NPs in detail. A final section on the perspectives and the possible evolution within the synthesis of such nanosystems is also given.

Condensation and Polymerization Reactions: Routes Based on the Sol-Gel Approach
Sol-gel synthesis is considered as one of the traditional synthetic strategies of inorganic solids, including inorganic polymers and ceramics [30]. Sol-gel syntheses starts with a homogeneous liquid solution of the precursors that undergo hydrolysis and condensation to form both a colloidal suspension (sol) and, later, under appropriate conditions leading to an increase in the viscosity, a gel [31]. Whether gelation or precipitation eventually occurs is dependent on the overall reaction kinetics which can be controlled by reaction parameters such as pH gradients, relative concentrations of the reactants, temperature, and speed and order of mixing the reactants. Gels are usually favored by slower reaction conditions [32].
Sol-gel routes thus comprise up to five different steps: hydrolysis and polycondensation of molecular precursors, usually metal alkoxides such as tetraethyl orthosilicate (TEOS) and titanium isopropoxide, or other hydrolysable and condensable species [33], followed by aging, drying, and a possible eventual thermal decomposition or calcination ( Figure 2) [34].

Condensation and Polymerization Reactions: Routes Based on the Sol-Gel Approach
Sol-gel synthesis is considered as one of the traditional synthetic strategies of inorganic solids, including inorganic polymers and ceramics [30]. Sol-gel syntheses starts with a homogeneous liquid solution of the precursors that undergo hydrolysis and condensation to form both a colloidal suspension (sol) and, later, under appropriate conditions leading to an increase in the viscosity, a gel [31]. Whether gelation or precipitation eventually occurs is dependent on the overall reaction kinetics which can be controlled by reaction parameters such as pH gradients, relative concentrations of the reactants, temperature, and speed and order of mixing the reactants. Gels are usually favored by slower reaction conditions [32].
Sol-gel routes thus comprise up to five different steps: hydrolysis and polycondensation of molecular precursors, usually metal alkoxides such as tetraethyl orthosilicate (TEOS) and titanium isopropoxide, or other hydrolysable and condensable species [33], followed by aging, drying, and a possible eventual thermal decomposition or calcination ( Figure 2) [34]. Inorganics 2021, 9, 58 4 of 24 Figure 2. General strategy in the sol-gel synthesis of materials. An appropriate control on the hydrolysis, condensation, and calcination steps may lead to nanostructured materials. Condensation reactions starting from tetraethylorthosilicate (TEOS) and resorcinol/formaldehyde for the synthesis of SiO2 and C-based materials, respectively, are shown. Adapted with permission from [35]. Copyright the Royal Society of Chemistry, 2016.
Although this method is traditionally associated with the synthesis of dense films or particles of widely used inorganic materials such as TiO2, SnO2, WO3, ZrO2, SiO2, and C-based structures, an appropriate control on some reaction parameters may lead to the production of uniform nanostructures. However, it should be considered that such reaction variables are often complex systems. Possible strategies rely on the design of appropriate precursors and on the use of additives and/or templates. Importantly, the obtained nanostructures should be thermally stable to withstand high temperature post-treatments.
Two of the key parameters during the polymerization and gelation in sol-gel processes are the hydrolysis and condensation. In some cases, uniform nanostructures can be produced by adjusting both hydrolysis and condensation rates. This can be achieved by using the appropriate precursors. In practice, this means that several precursors should be tested and studied systematically to obtain uniform nanostructures. In some cases some general rules may be taken into account. For example, a slow hydrolysis rate, compared with condensation, usually gives rise to more linear polymeric structures and weakly cross-linked gels, whereas a faster hydrolysis is more associated with more isotropic polymeric structures and highly branched clusters. This is well known for silica, in which the acidic or basic catalysts have a significant role in the structure of the resulting gel network [36]. Under some circumstances, the hydrolysis rate can be modified by selecting an appropriate precursor. For example, 1D metal oxide nanowires of TiO2, SnO2, In2O3, and PbO can be produced via a sol-gel route starting from metal glycolate, which shows a lower hydrolysis rate than their transition metal alkoxide counterparts [37]. In comparison, faster hydrolysis rate is shown by precursors such as tetra butyl titanate with acidic catalysis which is associated with the production of 3-4 nm TiO2 nanospheres [38] (Figure 3).  General strategy in the sol-gel synthesis of materials. An appropriate control on the hydrolysis, condensation, and calcination steps may lead to nanostructured materials. Condensation reactions starting from tetraethylorthosilicate (TEOS) and resorcinol/formaldehyde for the synthesis of SiO 2 and C-based materials, respectively, are shown. Adapted with permission from [35]. Copyright the Royal Society of Chemistry, 2016.
Although this method is traditionally associated with the synthesis of dense films or particles of widely used inorganic materials such as TiO 2 , SnO 2 , WO 3 , ZrO 2 , SiO 2 , and C-based structures, an appropriate control on some reaction parameters may lead to the production of uniform nanostructures. However, it should be considered that such reaction variables are often complex systems. Possible strategies rely on the design of appropriate precursors and on the use of additives and/or templates. Importantly, the obtained nanostructures should be thermally stable to withstand high temperature post-treatments.
Two of the key parameters during the polymerization and gelation in sol-gel processes are the hydrolysis and condensation. In some cases, uniform nanostructures can be produced by adjusting both hydrolysis and condensation rates. This can be achieved by using the appropriate precursors. In practice, this means that several precursors should be tested and studied systematically to obtain uniform nanostructures. In some cases some general rules may be taken into account. For example, a slow hydrolysis rate, compared with condensation, usually gives rise to more linear polymeric structures and weakly crosslinked gels, whereas a faster hydrolysis is more associated with more isotropic polymeric structures and highly branched clusters. This is well known for silica, in which the acidic or basic catalysts have a significant role in the structure of the resulting gel network [36]. Under some circumstances, the hydrolysis rate can be modified by selecting an appropriate precursor. For example, 1D metal oxide nanowires of TiO 2 , SnO 2 , In 2 O 3 , and PbO can be produced via a sol-gel route starting from metal glycolate, which shows a lower hydrolysis rate than their transition metal alkoxide counterparts [37]. In comparison, faster hydrolysis rate is shown by precursors such as tetra butyl titanate with acidic catalysis which is associated with the production of 3-4 nm TiO 2 nanospheres [38] (Figure 3). The use of additives, which can either be small molecules or polymers, is common in sol-gel syntheses. They are normally used to modify the aqueous hydrolysis chemistry of metal ions by forming stable aqueous metal complexes. Citrate, ethylenediaminetetraacetic acid (EDTA), other organic acids, urea, and their mixture (for example citrate and ethylene glycol, base of the Pechini synthesis) are some of the frequently used additives in sol-gel synthesis, showing, in some cases, some applications and advantages within the sol-gel chemistry. From the perspective of nanostructuration and morphology control, it should be considered that the presence of additives during the sol-gel process, including polymers, may create a controlled or hierarchical porosity. After the gel formation, the remaining solvent space between the solid network represents the potential pore space after drying. In fact, the gel formation can be considered as a phase separation process between two heterogeneous phases: a solid network and a solution phase. This phase separation, and thus the eventual porosity of the structure, can, in some cases, be controlled by adding certain additives, and it is determined by their interaction or affinities with both the precursors and the solvent [39]. For example, poly (ethylene oxide) or poly (acrylic acid) are typical polymers used for the synthesis of porous silica [40]. By optimizing the timing between the phase separation and the sol-gel transition, as well as the stability of the different heterogeneous phases, gels with a controlled porous structure can be obtained ( Figure 4A). After the removal of the solvent and careful controlled drying that preserve this morphology (i.e., drying with supercritical fluids or freeze drying to obtain aero-or cryo-gels, respectively), followed in some cases by calcination, hierarchically porous monoliths structures with pores resembling the solvent phase and solid architectures can be produced [35] ( Figure 4B).  The use of additives, which can either be small molecules or polymers, is common in sol-gel syntheses. They are normally used to modify the aqueous hydrolysis chemistry of metal ions by forming stable aqueous metal complexes. Citrate, ethylenediaminetetraacetic acid (EDTA), other organic acids, urea, and their mixture (for example citrate and ethylene glycol, base of the Pechini synthesis) are some of the frequently used additives in sol-gel synthesis, showing, in some cases, some applications and advantages within the sol-gel chemistry. From the perspective of nanostructuration and morphology control, it should be considered that the presence of additives during the sol-gel process, including polymers, may create a controlled or hierarchical porosity. After the gel formation, the remaining solvent space between the solid network represents the potential pore space after drying. In fact, the gel formation can be considered as a phase separation process between two heterogeneous phases: a solid network and a solution phase. This phase separation, and thus the eventual porosity of the structure, can, in some cases, be controlled by adding certain additives, and it is determined by their interaction or affinities with both the precursors and the solvent [39]. For example, poly (ethylene oxide) or poly (acrylic acid) are typical polymers used for the synthesis of porous silica [40]. By optimizing the timing between the phase separation and the sol-gel transition, as well as the stability of the different heterogeneous phases, gels with a controlled porous structure can be obtained ( Figure 4A). After the removal of the solvent and careful controlled drying that preserve this morphology (i.e., drying with supercritical fluids or freeze drying to obtain aeroor cryo-gels, respectively), followed in some cases by calcination, hierarchically porous monoliths structures with pores resembling the solvent phase and solid architectures can be produced [35] ( Figure 4B).  [41]; Copyright the American Chemical Society, 2006, and taken from [42]. Published by Elsevier. (B) Porous SiO2 silica monolith synthesised in the presence of polyethylene oxide [40]. Published by MDPI.
A step forward in this direction involves the use of templates. Some species can behave beyond an additive and self-organize during the sol-gel process. If the condensation of the sol-gel precursors takes place around such structures, and this template is eventually removed (i.e., by calcination), this geometry can be transferred to the final material, giving rise to structures that usually show an ordered and homogeneous pore distribution ( Figure 5A). This is for example the case of mesoporous silica, a family of materials that is characterized by an ordered distribution of the pores, presenting homogeneous sizes between 2 and 20 nm, high pore volume (ca. 1 cm 3 g −1 ), high surface area (ca. 1000 m 2 g −1 ), and has applications in nanomedicine and catalysis [43]. Templates can have a hard or a soft nature. Among the latter, surfactants or other amphiphillic species are frequently employed, which can be easily removed, for example by calcination. The geometry of the mesoporous nanostructure is mostly determined by the self-assembled structure adopted by the specie forming the template. Cationic surfactants, such as cetyltrimethylammonium bromide (CTAB), and amphiphilic block copolymers, such as Pluronics ® P103 y F127 (triblock copolymers based on poly ethylene oxide and polypropylene oxide), are employed as templates for the synthesis of mesoporous MCM-41 (with a hexagonal symmetry of the mesoporous structure), SBA-15 (hexagonal), and SBA-16 (cubic cage-structured), respectively. Some TEM images of different mesoporous silica NPs are shown in Figure 5B.  A step forward in this direction involves the use of templates. Some species can behave beyond an additive and self-organize during the sol-gel process. If the condensation of the sol-gel precursors takes place around such structures, and this template is eventually removed (i.e., by calcination), this geometry can be transferred to the final material, giving rise to structures that usually show an ordered and homogeneous pore distribution ( Figure 5A). This is for example the case of mesoporous silica, a family of materials that is characterized by an ordered distribution of the pores, presenting homogeneous sizes between 2 and 20 nm, high pore volume (ca. 1 cm 3 g −1 ), high surface area (ca. 1000 m 2 g −1 ), and has applications in nanomedicine and catalysis [43]. Templates can have a hard or a soft nature. Among the latter, surfactants or other amphiphillic species are frequently employed, which can be easily removed, for example by calcination. The geometry of the mesoporous nanostructure is mostly determined by the self-assembled structure adopted by the specie forming the template. Cationic surfactants, such as cetyltrimethylammonium bromide (CTAB), and amphiphilic block copolymers, such as Pluronics ® P103 y F127 (triblock copolymers based on poly ethylene oxide and polypropylene oxide), are employed as templates for the synthesis of mesoporous MCM-41 (with a hexagonal symmetry of the mesoporous structure), SBA-15 (hexagonal), and SBA-16 (cubic cage-structured), respectively. Some TEM images of different mesoporous silica NPs are shown in Figure 5B. A step forward in this direction involves the use of templates. Some species can behave beyond an additive and self-organize during the sol-gel process. If the condensation of the sol-gel precursors takes place around such structures, and this template is eventually removed (i.e., by calcination), this geometry can be transferred to the final material, giving rise to structures that usually show an ordered and homogeneous pore distribution ( Figure 5A). This is for example the case of mesoporous silica, a family of materials that is characterized by an ordered distribution of the pores, presenting homogeneous sizes between 2 and 20 nm, high pore volume (ca. 1 cm 3 g −1 ), high surface area (ca. 1000 m 2 g −1 ), and has applications in nanomedicine and catalysis [43]. Templates can have a hard or a soft nature. Among the latter, surfactants or other amphiphillic species are frequently employed, which can be easily removed, for example by calcination. The geometry of the mesoporous nanostructure is mostly determined by the self-assembled structure adopted by the specie forming the template. Cationic surfactants, such as cetyltrimethylammonium bromide (CTAB), and amphiphilic block copolymers, such as Pluronics ® P103 y F127 (triblock copolymers based on poly ethylene oxide and polypropylene oxide), are employed as templates for the synthesis of mesoporous MCM-41 (with a hexagonal symmetry of the mesoporous structure), SBA-15 (hexagonal), and SBA-16 (cubic cage-structured), respectively. Some TEM images of different mesoporous silica NPs are shown in Figure 5B. The most important feature of mesoporous materials is perhaps their ability to incorporate molecules or species into their pores. Molecules of interest can be incubated with the mesoporous materials and, under some circumstances, they may be absorbed onto their porous surface. In the case of mesoporous silica, this process is then controlled by the interactions between such molecules and the remaining surface silanol groups (-SiOH) on the silica [45]. The incorporation of the desired species can also be carried out by designing additional reactions consisting of the condensation of such silanol groups with alkoxyor chloro-silanes containing the additional desired moieties (grafting) [46], although this usually demands harsh reaction conditions. Moreover, an exact and controlled functionalization of the resulting surface may be difficult. An appropriate design of the molecular precursor before the sol-gel synthesis can be used to either provide the structure with additional reactive anchors for subsequent functionalization, or even to better introduce the desired loading group. In both cases, these moieties will be eventually present in the surface of the mesoporous material. To do so, a co-condensation strategy of the original molecular precursors with an optimized amount of a modified one containing the desired moieties can be carried out in the presence of a template, eventually resulting in the incorporation of new anchors such as N 3 moieties, suitable for effective conjugation with species containing alkyne groups (example of click chemistry [47]), or in more controlled and homogeneous distribution desired cargo within the mesoporous structure ( Figure 6).
In some cases, the term 'ship-in-a-bottle' approach refers to the loading of smaller precursors (active or guest species, usually salts or organometallics) into pre-formed porous host materials via solution-based, gas-phase, or mechanical-mixing impregnation, followed by either thermal/photochemical decomposition or redox reaction (with either strong redox reagents, e.g., hydrazine and NaBH 4 , or high-temperature treatment in reducing atmosphere, e.g., H 2 ) [48]. This approach has been used for the preparation of hybrid composite nanostructures based on zeolites [49][50][51] and MOFs [52], with applications in gas separation, CO 2 capture, and catalysis, among others. On the other hand, the opposite "bottle around ship" or "templated synthesis" approach consists of the assembly of the host material around the active or guest species [53,54].
Particular examples of templates are solid particles that can be easily dissolved under appropriate conditions. This is in fact a strategy for the synthesis of silica capsules, in which the molecular precursor, usually TEOS, is condensed on sacrificial CaCO 3 particles. These cores can be eventually dissolved in mild conditions, giving rise to SiO 2 capsules in which different molecules can be incorporated, with typical applications in drug delivery [57,58]. Hybrid organic-inorganic materials are also accessible by sol-gel chemistry. For example, sol-gel polymerization of silica and titania alkoxides, and others, on previously formed chitosan hydrocolloids or spheres can be used for the synthesis of chitosan-SiO 2 and TiO 2 hybrid materials yielding, after supercritical drying, high-surface-area porous materials with reactive surface and applications in catalysis [59,60].
Phase separation induced by the presence of additives and templating strategies combined with sol-gel processing can be used for the synthesis of porous nanostructured ceramics. For example, different porous structures of metal oxide systems such as Ce 0.5 Mg 0.5 O 1.5 , CeO 2 , Mn 3 O 4 and Fe 2 O 3 /Fe 3 O 4 synthesized through a Pechini-type approach can be produced by adjusting the malic acid and glycerine ratio, which are used as additives, in the presence of a poly(methyl methacrylate) (PMMA) colloidal crystal template. The resulting structures range from microspheres to bicontinuous networks and three-dimensionally ordered macroporous (3DOM) materials. In this case, the degree of polymerization of the polyester network, which can be controlled through tailoring the reagent imbalance, was assigned to be the predominant controlling factor of the system microstructural evolution [61]. Particular examples of templates are solid particles that can be easily dissolved under appropriate conditions. This is in fact a strategy for the synthesis of silica capsules, in which the molecular precursor, usually TEOS, is condensed on sacrificial CaCO3 particles. These cores can be eventually dissolved in mild conditions, giving rise to SiO2 capsules in which different molecules can be incorporated, with typical applications in drug delivery [57,58]. Hybrid organic-inorganic materials are also accessible by sol-gel chemistry. For example, sol-gel polymerization of silica and titania alkoxides, and others, on previously formed chitosan hydrocolloids or spheres can be used for the synthesis of chitosan-SiO2 and TiO2 hybrid materials yielding, after supercritical drying, high-surface-area porous materials with reactive surface and applications in catalysis [59,60].
Phase separation induced by the presence of additives and templating strategies combined with sol-gel processing can be used for the synthesis of porous nanostructured ceramics. For example, different porous structures of metal oxide systems such as Ce0.5Mg0.5O1.5, CeO2, Mn3O4 and Fe2O3/Fe3O4 synthesized through a Pechini-type approach can be produced by adjusting the malic acid and glycerine ratio, which are used A B Figure 6. (A) Co-condensation strategies for the synthesis of mesoporous silica nanoparticles with controlled and homogeneous N 3 anchors for further click functionalization. Adapted with permission of [55]. Copyright the American Chemical Society, 2012, and (B) bulky organic groups such as imidazolium groups that can be used for a more controlled absorption of Pd. Reproduced with permission of [56]. Copyright the Royal Society of Chemistry, 2015.

Colloidal Synthesis of Nanostructures
The colloidal chemistry is a powerful method for the synthesis of many different nanostructures, including metal, semiconductor, and oxide NPs. In this strategy, NPs are formed in solution, which usually offers a great control on their shape and size, allowing in many cases a narrow size distribution [62]. Moreover, synthesis methods for the production of anisotropic particles [63] as well as complex structures such as hollow structures [64], core-shell particles [65], and particles showing regions with different surfaces, chemistries, and properties (for example Janus NPs [66]) can be designed. The major drawback of this strategy is the possibility of particle aggregation. Colloids are defined as dispersions of one material, typically particles or droplets in a size range from 1 nm to 1 µm, in another substance, which can be solid, liquid, or gas [67]. Colloids are thermodynamically unstable with respect to the bulk, and particles tend to agglomerate and aggregate. However, colloidal particles may be stabilized by either binding long-chained molecules to the particle surface, giving rise to steric repulsion and solubilization in non-polar solvents, or by surface charge stabilization, which may give rise to electrostatic repulsion of the particles. For this reason, colloidal inorganic NPs may be considered as hybrid inorganicorganic systems consisting of an inorganic core and an organic shell. The presence of this surface organic shell, and especially the possibility of doing surface chemistry with it (i.e., functionalization) [68], is maybe one of the most interesting features of such structures.
The classical nucleation and growth model, developed by Lamer in the 1950s for colloidal sulfur [69], is traditionally used to explain the synthesis of colloidal particles from a solution. It considers the evolution of the reactant (or atom) concentrations with time, describing three different phases: saturation and increase in the precursor concentration, nucleation of very small particles, and particle growth. This model establishes that the separation of nucleation and growth processes are necessary to obtain monodisperse particles by homogeneous precipitation, and that some variables, such as the precursor concentrations, number of formed nuclei, and viscosity of the media and temperature (which affect diffusion), can be optimized for a better control on the final morphology of the NPs. A more detailed explanation of this model is given in the section dedicated to metal-organic frameworks.
Solid nuclei can be produced either by reduction or decomposition of a precursor. The former is usually employed for the synthesis of metallic plasmonic NPs. In this case, the reduction in precursors such as HAuCl 4 , AgNO 3 or Pt(acac) 2 with sodium citrate, sodium borohydride, sodium ascorbate, or sodium thiosulfate, among others, gives rise to solid metal nuclei. Although the strong or mild nature of the reductant may have an influence, additives usually play a key role in the final morphology of the plasmonic particles, acting as shape-directing reagents [70]. For example, the presence of species such as CTAB, polymers, and even halide anions during the growth step of the synthesis may lead to anisotropic nanoparticles by either inducing kinetically controlled NPs growth or blocking some growing facets [71]. For these systems, the nucleation and growth are, in many cases, separated in two different synthetic steps. This is known as the seed-mediated strategy, which usually avoids additional nucleation events and thus provides a better control on the particle morphology through a more controlled reaction kinetics [72,73]. Typical synthesis of plasmonic NPs [74] can be performed in both aqueous [75,76] or organic solvents [77]. The latter usually offers higher possible synthesis temperatures, higher precursor concentrations, as well as a wider selection of hydrophobic additives, which may better stabilize or control the morphology (i.e., capping) of the NPs, although they render hydrophobic NPs which may demand additional post-synthetic treatment. Some Au and Ag NPs with different morphologies are shown in Figure 7. For example, the deposition of gold onto previously formed gold seeds by reduction with ascorbic acid of solutions containing HAuCl 4 , CTAB and small amounts of AgNO 3 gives rise to gold nanorods, while the concentration of the additive poly(vinylpyrrolidone) (PVP) or the pH controls the morphology of silver NPs. drophobic additives, which may better stabilize or control the morphology (i.e., capping) of the NPs, although they render hydrophobic NPs which may demand additional post-synthetic treatment. Some Au and Ag NPs with different morphologies are shown in Figure 7. For example, the deposition of gold onto previously formed gold seeds by reduction with ascorbic acid of solutions containing HAuCl4, CTAB and small amounts of AgNO3 gives rise to gold nanorods, while the concentration of the additive poly(vinylpyrrolidone) (PVP) or the pH controls the morphology of silver NPs. Reproduced with permission of [79]. Copyright the American Chemical Society, 2011. (D) Ag NPs of different morphologies synthesized in water at different pH in the presence of different amounts of sodium citrate. Taken from [80]. Published by MDPI. All the syntheses correspond to seed-mediated strategies.
Precursor decompositions constitute the second group of strategies for the formation of solid nuclei. Such reactants usually release cations or anions into the solution, causing precipitation. As a general rule, the synthesis of uniform NPs requires a slow and controlled release or cations or/and anions into the reacting media, followed by an appropriate kinetics [81], which may be determined after the experimental optimization of the reaction conditions. This is the basic of the homogeneous precipitation. The molecular design of the precursor is often a key factor in the synthesis of uniform nanostructures, given that, apart from the slow and controlled release of the cations or anions, it may prevent uncontrolled decompositions and precipitations and second nucleation events, Precursor decompositions constitute the second group of strategies for the formation of solid nuclei. Such reactants usually release cations or anions into the solution, causing precipitation. As a general rule, the synthesis of uniform NPs requires a slow and controlled release or cations or/and anions into the reacting media, followed by an appropriate kinetics [81], which may be determined after the experimental optimization of the reaction conditions. This is the basic of the homogeneous precipitation. The molecular design of the precursor is often a key factor in the synthesis of uniform nanostructures, given that, apart from the slow and controlled release of the cations or anions, it may prevent uncontrolled decompositions and precipitations and second nucleation events, and may also provide colloidal stability to the precipitated nuclei. This is relevant in the synthesis of metal or metal oxide NPs through the organometallic approach, which uses organometallic and metal-organic complexes as precursors. Nanostructures are formed when the precursors decompose in the presence of appropriate ligands, whose amount is also optimized [82]. For example, the decomposition of bis(dibenzylideneacetone)platinum ([Pt(dba) 2 ], a neutral Pt complex) at −80 • C with H 2 in the presence of controlled amounts of N-heterocyclic thiones (NHT) is used for the synthesis and stabilization of approxi-mately 2 nm Pt NPs. Sub-stoichiometric amounts of the ligands prevent the formation of a new organometallic compound, induce aggregation and thus lead to the precipitation of small Pt NPs ( Figure 8A) [83]. Other examples are the synthesis of highly monodisperse Sn NPs, which are produced after the reduction in a Sn-oleylamido complex, previously designed from the reaction of lithium oleylamide and SnCl 2 ( Figure 8B) [84]. In many cases, highly uniform NPs can be synthesized in organic solvents of high boiling points such as octadecene, in the presence of oleic acid, oleylamine, or mixtures or analogous additives [85,86], although it should be noticed that the resulting particles are hydrophobic. Analogously, a Cd-hexylphosphonic acid (HPA)/trioctylphosphine oxide (TOPO) complex synthesized from CdO is the appropriate precursor to obtain uniform semiconductor CdSe NPs, given that it is more prone to a controlled decomposition and is also suitable for larger-scale synthesis ( Figure 8C) [87]. and may also provide colloidal stability to the precipitated nuclei. This is relevant in the synthesis of metal or metal oxide NPs through the organometallic approach, which uses organometallic and metal-organic complexes as precursors. Nanostructures are formed when the precursors decompose in the presence of appropriate ligands, whose amount is also optimized [82]. For example, the decomposition of bis(dibenzylideneacetone)platinum ([Pt(dba)2], a neutral Pt complex) at −80 °C with H2 in the presence of controlled amounts of N-heterocyclic thiones (NHT) is used for the synthesis and stabilization of approximately 2 nm Pt NPs. Sub-stoichiometric amounts of the ligands prevent the formation of a new organometallic compound, induce aggregation and thus lead to the precipitation of small Pt NPs ( Figure 8A) [83]. Other examples are the synthesis of highly monodisperse Sn NPs, which are produced after the reduction in a Sn-oleylamido complex, previously designed from the reaction of lithium oleylamide and SnCl2 ( Figure 8B) [84]. In many cases, highly uniform NPs can be synthesized in organic solvents of high boiling points such as octadecene, in the presence of oleic acid, oleylamine, or mixtures or analogous additives [85,86], although it should be noticed that the resulting particles are hydrophobic. Analogously, a Cd-hexylphosphonic acid (HPA)/trioctylphosphine oxide (TOPO) complex synthesized from CdO is the appropriate precursor to obtain uniform semiconductor CdSe NPs, given that it is more prone to a controlled decomposition and is also suitable for larger-scale synthesis ( Figure 8C) [87]. Molecular species such as yttrium acetylacetonate (Y(acac) 3 ) [88,89] and sodium tetrafluoroborate (NaBF 4 ) [90] are appropriate precursors for the synthesis of Y-based fluoride NPs by homogenous precipitation, since the Y 3+ and F − ions are slowly released upon heating. Ionic liquid are good alternatives, as they can either act as precursors (for example, the ionic liquid 1-butyl-2-methylimidazolium tetrafluoroborate) (BMIMBF 4 also releases slowly fluoride anions when heating), and solvents [91,92]. In other cases, metal complexes can be formed, as it occurs for calcium citrate complexes, which also slowly release Ca 2+ into the solution at elevated temperature [93], and rare earth-citrate complexes [94,95], used as precursors for the synthesis of uniform rare earth-based NPs.
Other synthetic variables that may be taken into account are the presence and concentration of additives, which may also act as capping and/or dispersing agents and may thus play a role in the final morphology of the NPs [70]. For example, similar to the synthesis of anisotropic metal NPs, the presence of CTAB in the reaction media has been associated, in some cases, with the synthesis of anisotropic ceramic nanostructures, as it is the case of strontium hydroxyapatite nanorods [96][97][98]. At this point, the additives should show some affinity for the NPs surface. For example, the surface of Au and Ag NPs and other plasmonic materials show affinity toward additives containing thiols, amines, and cyanides; species containing carboxyl and hydroxyl groups are usually appropriate for oxides, whereas molecules with thiols, hydroxyl, and amino moieties may be appropriate for semiconductor NPs [68]. In some cases, additives do not only act as structure directing species, but also as functionalizing agents, provided they are eventually situated on the NP surface (in some cases the term "one-pot" synthesis is used to refer this) [99]. This may prevent NPs from aggregation, thus enhancing their colloidal stability, and also offer reactive anchors on the NP surface for conjugation with additional functional species.
The reagent concentrations, the synthesis temperature, the pH of the reaction, the heating method (microwave or conventional oven), and the solvent composition are other variables that may play a key role in the optimization of the synthesis routes yielding uniform NPs [100,101]. Solvents such as polyols may give rise to changes in both the diffusion and dielectric constant of the reaction media; in some cases, they can prevent uncontrolled precipitation by forming stable complexes with the metals [102], as well as act as reducing agents, as in the case of the synthesis of Ag NPs [103].
Syntheses at atmospheric pressure can be performed in water or organic solvents such as alcohols, polyols, and solvents of higher boiling points at a temperature below the boiling point of the solvent, whereas hydro-or solvothermal-based methods are those carried out in closed vessels under autogenous pressure above the boiling point of the solvent [104]. They have been applied for the synthesis of many different nanomaterials [105]. Ionothermal syntheses use ionic liquids simultaneously as both the solvent and potential template or the structure-directing agent in the formation of solids, and have been applied for the synthesis of porous materials such as zeolites, MOFs, and inorganic-organic hybrid nanostructures [106,107]. Mechanochemical processes use mechanical forces such as compression, shear, or friction for the synthesis of materials, and have recently emerged as an alternative to traditional routes for nanomaterials preparation [108].

Synthesis of Metal-Organic Frameworks (MOF)-Based Nanomaterials
Metal-organic frameworks (MOFs), a representative family of hybrid inorganicorganic materials, are currently one of the hot topics in the field of hybrid porous solids [109]. Although MOFs were discovered back in 1965, the acronym "MOF" was first introduced by Yaghi and co-workers in 1999 [110], and it was after their studies that highlighted the true potential of these materials when MOFs started to attract great interest. MOFs, also called porous coordination polymers, are self-assembled structures composed of metal nodes (metal ions or clusters) and polydentate organic ligands (mainly carboxylates, imidazolates, or phosphonates) [111][112][113]. They are obtained via "reticular synthesis", a bottom-up synthetic approach in which predetermined ordered structures are produced by selecting the appropriate molecular building blocks. The resulting ordered structural motifs, similar to cage-like structures, provide them with a high internal surface area and porosity, which are the key features exploited in most of their applications in fields as diverse as gas storage and separation [114][115][116], molecular sieving [117], energy storage and conversion [118], sensing [119], catalysis [120], and controlled delivery of active species (e.g., drugs [121,122] and fertilizers [123]).
The synthetic process generally consists of mixing the molecular building blocks (i.e., precursors) in a solvent (commonly methanol, dimethylformamide, or water); it then either leaves the mixture undisturbed at room temperature during a period of time when the self-assembly process takes place, or heats the mixture by conventional heating or through other energy sources, such as microwave or ultrasound, at an appropriate temperature and for a specific time. The incorporation of a modulator agent (i.e., additive) into the synthetic mixture is a common strategy to achieve a fine control over the self-assembly process, and in ensuring reproducibility of the physical properties such as crystallinity, particle size, morphology, porosity, defectivity, and surface chemistry of MOFs [124], as it will be shown later with some illustrative examples. It should also be noted that, as in colloidal synthesis, the experimental conditions (e.g., metal-to-ligand ratio, metal source, solvent, presence of bases or pH, capping agent, temperature, and reaction time) have a strong influence on the final structure of the MOFs, as well as on their physicochemical properties. Thus, the rational synthesis of MOFs requires a careful choice of synthetic strategies, and the optimization of the experimental parameters. It is also important to remark that the ease of synthesis of many MOF's types is a large bonus, which makes them attractive alternatives to the traditional porous materials.
A special feature of MOFs associated with their modular nature is their wide tunability. The topologies, porosities, functionalities, and surface properties of MOFs can be manipulated by playing with different metal nodes and organic linkers, and also by means of post-synthetic modifications [125]. Indeed, nowadays, they are a huge family of MOFs with about 20,000 different structures (as reported in the Cambridge database [113]) and with quite diverse properties, which can be predefined on purpose thanks to the help of computational studies. This is possible because of the periodic structure of crystalline MOFs that allows one to know precisely the position that each atom within the crystal lattice and, therefore, its coordination environment, bond distances, electronic properties of metal ions, etc. [126]. Computational methods are nowadays used not only to understand the formation and ultimate properties of MOFs, but also to predict some properties, as well as establishing structure-activity relationships. Moreover, in the catalysis field, these computational methods are a powerful tool for explaining reaction mechanisms and observed selectivities, among other aspects.
Despite the tremendous growth in the number of MOFs synthesized to date, the mechanism of MOF formation is not yet fully understood. In order to control the structures and functionalities of MOFs, it is really important to understand the interactions between the constituent building blocks and the physical factors governing the self-assembly process [127]. Several experimental and theoretical studies have pointed out that the selfassembly process of a MOF system is a stochastic and multistage ordering process [128], and that multiple intermediates can be formed during this process [129,130]. Despite this, from a simplified point of view, the LaMer model for the synthesis of colloidal particles can also be applied to explain the formation of MOF particles in solution ( Figure 9). As stated previously in Section 3, the process consists of two stages, namely nucleation and growth. During the initial state of nucleation, the concentration of the reactive species increases until reaching the critical concentration of nucleation (C nuc ). After this point, the reactive species start to assemble and form nuclei, which results in a decrease in monomers in the solution. Afterwards, the growth of the particles takes place, and the size increases with time. Eventually, the system reaches the saturation point (C sat ), at which point the growth and solvation of particles reach equilibrium. The nucleation stage is critical in controlling the size of MOF particles; rapid formation of nuclei leads to smaller MOF particles.
After this point, the reactive species start to assemble and form nuclei, which results in a decrease in monomers in the solution. Afterwards, the growth of the particles takes place, and the size increases with time. Eventually, the system reaches the saturation point (Csat), at which point the growth and solvation of particles reach equilibrium. The nucleation stage is critical in controlling the size of MOF particles; rapid formation of nuclei leads to smaller MOF particles. MOF's crystalline particles can be synthesized at different scales; from macro-to micro-and nano-scale. When reduced to the nanoregime, MOF nanocrystals (i.e., nanoscale MOFs, or nano-MOFs) can offer significantly enhanced properties compared to their bulk counterparts, such as controllable diffusion kinetics, high ratio of exposed active sites, and efficient confinement of redox centers. The possibility of having nano-MOFs has allowed novel applications where a specific size is required, as is the case of biomedical applications [131] and nanocatalysis [132]. MOF nanoparticles can also serve as basic building blocks for the assembly of superstructures with complicated morphologies, that is, hierarchical assemblies [133]. There are several synthetic methods for scaling down the MOFs to the nanoscale [134,135], which can be included in one of the two following approaches: (i) placement of metal ions and organic linkers in confined spaces by using emulsions, templates, or surfactants to confine the MOF formation within the nanospace, restricting the crystal growth and thus leading to smaller MOF sizes; or (ii) promotion of nucleation over crystal growth, for example by tuning the reactants concentration or introducing modulators. Alternatively, the use of microwave and ultrasound synthesis are also strategies to accelerate the nucleation stage of MOFs. However, obtaining uniform nanoscale MOF particles is not a simple task, and it has not yet been achieved for some MOF types. During a typical MOF synthesis, it is common to obtain a mixture of particles with various sizes and/or morphologies (i.e., low homogeneity), which makes it difficult to control the properties of the material on a large scale. Furthermore, given the difficulty of purifying MOF nanoparticles post-synthetically, the optimization of synthetic methods with a high control on the size and monodispersity of MOF's crystalline particles can be synthesized at different scales; from macro-to micro-and nano-scale. When reduced to the nanoregime, MOF nanocrystals (i.e., nanoscale MOFs, or nano-MOFs) can offer significantly enhanced properties compared to their bulk counterparts, such as controllable diffusion kinetics, high ratio of exposed active sites, and efficient confinement of redox centers. The possibility of having nano-MOFs has allowed novel applications where a specific size is required, as is the case of biomedical applications [131] and nanocatalysis [132]. MOF nanoparticles can also serve as basic building blocks for the assembly of superstructures with complicated morphologies, that is, hierarchical assemblies [133]. There are several synthetic methods for scaling down the MOFs to the nanoscale [134,135], which can be included in one of the two following approaches: (i) placement of metal ions and organic linkers in confined spaces by using emulsions, templates, or surfactants to confine the MOF formation within the nanospace, restricting the crystal growth and thus leading to smaller MOF sizes; or (ii) promotion of nucleation over crystal growth, for example by tuning the reactants concentration or introducing modulators. Alternatively, the use of microwave and ultrasound synthesis are also strategies to accelerate the nucleation stage of MOFs. However, obtaining uniform nanoscale MOF particles is not a simple task, and it has not yet been achieved for some MOF types. During a typical MOF synthesis, it is common to obtain a mixture of particles with various sizes and/or morphologies (i.e., low homogeneity), which makes it difficult to control the properties of the material on a large scale. Furthermore, given the difficulty of purifying MOF nanoparticles post-synthetically, the optimization of synthetic methods with a high control on the size and monodispersity of nano-MOFs is of great importance. As an example of the control of the MOF crystal size, the zeolitic imidazolate framework-8 (ZIF-8) can be synthesized with different particle sizes (from few nanometers to micrometers) by adjusting the concentration of a surfactant, specifically CTAB, that acts as a growth inhibitor ( Figure 10A) [136]. Likewise, the reactivity of the Zn 2+ salt used as a precursor also has a strong influence on the size of the ZIF-8 particles, and varying the kinetic of the nucleation stage is also a common strategy to tune the MOF size [137]. Note that, regardless of the size or morphology of the ZIF-8 crystals, all of them present identical crystallinity, with a sodalite-type structure. However, changes in the particle size induce changes in stability and adsorption properties, as has been demonstrated through thermogravimetric analysis and Brunauer-Emmett-Teller (BET) surface area measurements. As a general trend, smaller MOF crystals exhibit higher surface areas and better catalytic activities, but lower stability.
ample, HKUST-1 can be selectively formed in different geometries (cube, cuboctahedron, and octahedron) by using modulators. Kitagawa and coworkers systematically investigated the effects of n-dodecanoic acid as a growth-blocking agent, which decelerates the crystal growth in the <100> direction and favors the <111> direction, leading to preferential formation of the cubic morphology [138]. In the case of ZIF-8, the crystal growth of a particle starts from an all <100> oriented cube that gradually evolves first into truncated rhombic dodecahedral shape and finally to rhombic dodecahedral shape, in which all the facets are <110> oriented ( Figure 10A). The addition of the surfactant CTAB in the ZIF-8 synthesis has an effect on the size of the crystal particles, as stated above, but it also works as a modulator of the particle shape [136]. Increasing the CTAB concentration suppresses the <100> growth of ZIF-8, leading to the formation of smaller and cubic-shaped crystals ( Figure 10B). This is due to the selective attachment of the hydrophobic tail of the CTAB molecules on the energetically favorable <100> facets.  Apart of the control of the size, synthesizing MOFs with specific morphologies is also challenging. In principle, the final shape of a MOF particle is the consequence of the Wulff's rule, where the slowest growing direction thermodynamically determines the final shape and the most stable facet orientation [136]. However, there are strategies to favor the crystal growth towards preferred orientations, and thus achieve a controllable growth of specific crystal faces. By adjusting the reaction conditions and/or by introducing growthblocking agents that inhibit a specific growth direction, the shape of the MOF particles can be tuned to nanospheres, nanocubes, nanorods, and nanoplates. As an example, HKUST-1 can be selectively formed in different geometries (cube, cuboctahedron, and octahedron) by using modulators. Kitagawa and coworkers systematically investigated the effects of n-dodecanoic acid as a growth-blocking agent, which decelerates the crystal growth in the <100> direction and favors the <111> direction, leading to preferential formation of the cubic morphology [138]. In the case of ZIF-8, the crystal growth of a particle starts from an all <100> oriented cube that gradually evolves first into truncated rhombic dodecahedral shape and finally to rhombic dodecahedral shape, in which all the facets are <110> oriented ( Figure 10A). The addition of the surfactant CTAB in the ZIF-8 synthesis has an effect on the size of the crystal particles, as stated above, but it also works as a modulator of the particle shape [136]. Increasing the CTAB concentration suppresses the <100> growth of ZIF-8, leading to the formation of smaller and cubic-shaped crystals ( Figure 10B). This is due to the selective attachment of the hydrophobic tail of the CTAB molecules on the energetically favorable <100> facets.
Taking a step further, post-synthetic bottom-up strategies have been used to obtain new morphologies or complex core-shell structures (MOF1@MOF2). Generally, these strategies consist of synthesizing the first MOF as a core followed with the growth of the second MOF on the pre-synthesized core particles. One of the first examples in this direction was reported by Matzger and coworkers in 2009, where IRMOF-3 was grown over cubic-shaped MOF-5 and vice versa [139]. They also demonstrated the possibility of growing a second MOF layer, yielding three-layered crystals made of two different MOFs in a Matryoshka doll-like or onion-like design ( Figure 11A). Similarly, Yamauchi and coworkers used the same strategy to produce core-shell ZIF-8@ZIF-67 particles, and investigated their transformation into porous carbon materials by pyrolysis maintaining the rhombic dodecahedral shape in both the core and shell [140]. Under the same pyrolysis conditions (800 • C in N 2 atmosphere for 3 h), the ZIF-8 was transformed into highly porous N-doped amorphous carbon (NC), whereas the ZIF-67 exhibited less porous but crystalline graphitic carbon (GC), Figure 11B. This NC@GC material presented good electrocatalytic activity for oxygen reduction reactions.
Taking a step further, post-synthetic bottom-up strategies have been used to obtain new morphologies or complex core-shell structures (MOF1@MOF2). Generally, these strategies consist of synthesizing the first MOF as a core followed with the growth of the second MOF on the pre-synthesized core particles. One of the first examples in this direction was reported by Matzger and coworkers in 2009, where IRMOF-3 was grown over cubic-shaped MOF-5 and vice versa [139]. They also demonstrated the possibility of growing a second MOF layer, yielding three-layered crystals made of two different MOFs in a Matryoshka doll-like or onion-like design ( Figure 11A). Similarly, Yamauchi and coworkers used the same strategy to produce core-shell ZIF-8@ZIF-67 particles, and investigated their transformation into porous carbon materials by pyrolysis maintaining the rhombic dodecahedral shape in both the core and shell [140]. Under the same pyrolysis conditions (800 °C in N2 atmosphere for 3 h), the ZIF-8 was transformed into highly porous N-doped amorphous carbon (NC), whereas the ZIF-67 exhibited less porous but crystalline graphitic carbon (GC), Figure 11B. This NC@GC material presented good electrocatalytic activity for oxygen reduction reactions. In addition to the above discussed synthetic strategies which rely on a bottom-up approach, there is also top-down approach, for example by exfoliation of large MOF crystals through ultrasonication, ball milling, and grinding. However, these top-down methods are much less applicable because of their intrinsic limitations, mainly the lack of precise control over the size and morphology of the obtained particles (samples with a high heterogeneity) and reproducibility issues. On the other hand, one interesting example reported by Maspoch and coworkers is the possibility of selectively changing the morphology of ZIFs (ZIF-8 and ZIF-67 nanocrystals) by an anisotropic wet-chemical etching strategy [141]. That is a top-down approach that controllably deconstructs the material to yield unprecedentedly shaped, hierarchically porous, or simply hollow crystals. They could demonstrate that (i) the etching occurs preferentially in the crystallographic directions richer in metal-ligand bonds; (ii) the etching rate tends to be faster on the crystal surfaces of higher dimensionality; and (iii) the pH of the etchant solution is the key to modulate the etching process. In addition to the above discussed synthetic strategies which rely on a bottom-up approach, there is also top-down approach, for example by exfoliation of large MOF crystals through ultrasonication, ball milling, and grinding. However, these top-down methods are much less applicable because of their intrinsic limitations, mainly the lack of precise control over the size and morphology of the obtained particles (samples with a high heterogeneity) and reproducibility issues. On the other hand, one interesting example reported by Maspoch and coworkers is the possibility of selectively changing the morphology of ZIFs (ZIF-8 and ZIF-67 nanocrystals) by an anisotropic wet-chemical etching strategy [141]. That is a top-down approach that controllably deconstructs the material to yield unprecedentedly shaped, hierarchically porous, or simply hollow crystals. They could demonstrate that (i) the etching occurs preferentially in the crystallographic directions richer in metal-ligand bonds; (ii) the etching rate tends to be faster on the crystal surfaces of higher dimensionality; and (iii) the pH of the etchant solution is the key to modulate the etching process.
In addition, to obtain structure-controllable synthetic routes, the synthesis of MOFs is rapidly evolving to be easier, faster, greener, and to obtain higher yields and scalingup methods with the consequent cost reduction (especially relevant from an industrial point of view). In this direction, microwave-assisted, sonochemical, mechanochemical, microfluidic, and continuous flow syntheses of MOFs are the most promising synthetic methods [142]. Compared to conventional heating techniques, the microwave-assisted method permits shorter heating durations (only a few minutes) due to the application of more concentrated and localized power, which results in increased nucleation and thus smaller particle sizes [143]. Likewise, ultrasound-assisted synthesis provides a localized high temperature and pressure generated by acoustic cavitation, which leads to enhanced nucleation, controlled particle morphology, and phase selectivity [143]. However, to date, microwave-and ultrasound-assisted methods are only applicable for a limited number of MOFs. The synthesis of MOFs by mecanochemistry implies the use of mechanical grinding (mechanical force) to provide the necessary energy and promote the reaction for the MOF formation [144]. Mechanochemical methods are solvent-free, which make them a convenient green and scalable alternative to prepare MOFs. Nevertheless, a high control of size and shape of the obtained crystals is quite difficult to achieve, and irreproducibility is the major drawback of mecanochemical synthetic routes. Continuous flow process for the synthesis of MOFs would scale up and improve the efficiency [145]. However, there are still important limitations and challenges to obtain MOFs with optimum properties, and, to date, there are only a few examples of successful synthesis for some MOF types. The concerted effort of chemists and engineers is key of success in this direction, and a lot of recent work is being focused on this goal.

Evolution and Perspectives
Although the number of protocols for the synthesis of uniform nanostructures has grown exponentially in the two last decades, there are still many challenges that currently demand the effort and the attention of chemists. Firstly, nanostructuration strategies should be extended to many more systems. This includes silicate, aluminate, and other refractory materials. The traditional synthesis of such materials often requires elevated temperatures, resulting in many cases in heterogeneous microparticles. Synthetic routes at milder conditions that provide a control on the particle morphologies for many material compositions are still demanded. Moreover, the design of synthetic protocols yielding more complex and hierarchical nanostructures, with the integration of different structures and functionalities in a same nanosystem, is another topic to better develop. Examples are core-shell nanoparticles, Matryoshka doll-like nanoparticles, and Janus nanoparticles.
The lack of routes for the synthesis of large amounts of inorganic and hybrid organicinorganic nanomaterials is one limiting factor, given that, in most cases, it hinders the transfer of nanostructures from the laboratory to the market and industry. The effect of higher precursor concentrations, and different reactor geometries and volumes on the particle morphology and homogeneity when compared to the laboratory scale, is yet to be studied and optimized. The design of protocols for the large-scale and cost-effective synthesis of nanoparticles, including faster and easier purification strategies, is thus one important current challenge.
As a general trend, alternative protocols to promote green synthesis are also highly desirable. This includes the use of chemicals with reduced toxicity and the design of reactions demanding milder synthetic conditions. Green chemistry protocols and biomimetic synthesis are some examples of the evolution within this topic.
Regarding syntheses based on polymerization and condensation, the development of a non-aqueous sol-gel chemistry is one of the possible evolutions of the sol-gel synthesis of nanomaterials. Given that the production of water is involved in the hydrolysis and condensation of metal alkoxides, the kinetics of the reactions is strongly dependent on water content. The design of non-aqueous condensation reactions may offer enhanced control on the kinetics, which may lead to a more controlled morphology of the nanostructures [146]. Examples of non-hydrolytic sol-gel chemistry include alkyl halide elimination, ether elimination, ester elimination, and aldol-like condensation [147]. Focusing on porous materials for catalysis, structures with abundant exposed active sites and highly accessible surfaces are also desirable.
Extensive efforts have already been devoted to developing efficient synthetic bottomup strategies for obtaining MOFs with controllable sizes and morphologies. However, this field of research is still in its infancy and there are still many challenges for further investigations. On the one hand, one important challenge is large-scale synthesis of MOFs due to the following reasons: high price of ligands for some MOFs, harsh synthetic conditions for diverse MOFs, low yields of most of the synthetic methods, and limited control of the structure and properties, among others. On the other hand, applications of conventional microporous MOFs are usually hampered by their limited pore sizes, especially in the fields of heterogeneous catalysis and cargo delivery, where large molecules have diffusion limitations. Therefore, the development of strategies to construct hierarchically porous MOFs, containing mesopores (2-50 nm) or even macropores (>50 nm) in addition to micropores (<2 nm), is of utmost importance. Moreover, benefiting from the knowledge gained from the MOF synthetic chemistry to date, much research is focused on the assembly of MOF nanostructures with uniform sizes and shapes into hierarchical superstructures, which can be used to construct electronic and photonic nanodevices. The functionalization and optimization of the surface reactions in hybrid systems to change, improve, or modify the properties of the nanostructures, thus affecting their colloidal stability, is another important point to consider. This demands a closer collaboration between both inorganic and organic chemists.
Last but not least, perhaps one of the major difficulties found in the laboratories of chemistry is the reproducibility. Although this is in fact a complex issue, given that many different parameters and variables can affect the chemical reactions, including the role played by impurities [148], some good practices might help. For example, full details of the reaction scheme, including in many cases "tricks" and the complete references of the used chemical reagents, could be given when reporting synthesis protocols of nanostructures.

Conflicts of Interest:
The authors declare no conflict of interest.