1. Introduction {#sec1-nanomaterials-10-00378}
===============

Developing sustainable energy is one of the most urgent tasks of humankinds. With the development of science and technology, the explosive growth of energy demand is making limited traditional fossil energy stretched thin. Among various types of sustainable energy, solar energy is the most abundant renewable energy source on earth. However, it is dilute, unequally distributed, and intermittent. Hence, to harness solar energy facilely, efficiently and economically remains a challenge \[[@B1-nanomaterials-10-00378]\]. Solar driven photocatalysis based on particulate photocatalysts is a potentially scale-up industrial and economically practical technology to convert solar energy into chemical energy. Since 1972, when Fujishima and Honda first reported the phenomenon of hydrogen generation from the decomposition of water by TiO~2~ photocatalysts, photocatalysis has gradually attracted the attention of academia and industry \[[@B2-nanomaterials-10-00378]\]. In 2001, Zou et al. \[[@B3-nanomaterials-10-00378]\] first discovered In~1-*x*~Ni*~x~*TaO~4~ photocatalyst with visible light activity for photolytic water splitting. The past two decades, various kinds of semiconductor photocatalysts have been widely studied, such as oxides \[[@B4-nanomaterials-10-00378],[@B5-nanomaterials-10-00378],[@B6-nanomaterials-10-00378],[@B7-nanomaterials-10-00378],[@B8-nanomaterials-10-00378],[@B9-nanomaterials-10-00378]\], sulfides \[[@B10-nanomaterials-10-00378],[@B11-nanomaterials-10-00378],[@B12-nanomaterials-10-00378],[@B13-nanomaterials-10-00378],[@B14-nanomaterials-10-00378]\], nitrides \[[@B15-nanomaterials-10-00378],[@B16-nanomaterials-10-00378],[@B17-nanomaterials-10-00378],[@B18-nanomaterials-10-00378]\], carbides \[[@B15-nanomaterials-10-00378],[@B19-nanomaterials-10-00378],[@B20-nanomaterials-10-00378],[@B21-nanomaterials-10-00378]\], etc. Domen's recent studies based on particulate photocatalyst sheets provide a possible way for the large-scale and practical photocatalytic water splitting \[[@B22-nanomaterials-10-00378],[@B23-nanomaterials-10-00378],[@B24-nanomaterials-10-00378]\].

A typical photocatalytic process mainly consists of three steps: (i) semiconductors absorb light of corresponding wavelength with appropriate bandgap; (ii) transition of photo induced carriers from valence band to conduction band; (iii) carrier migration to material surface for redox reaction with reactants \[[@B25-nanomaterials-10-00378]\]. However, the band gaps of most metal oxides are too large to avail adequate absorption of the majority of photons in the solar spectrum \[[@B26-nanomaterials-10-00378]\]. There are limitations in most semiconductor photocatalysts like fast charge carriers recombination, surface carrier recombination, as well as surface state pinning which prevent photogenerated carriers from participating in redox reaction \[[@B25-nanomaterials-10-00378]\]. In the study of particle photocatalysts, however, photocatalytic quantum efficiency of the bulk photocatalysts is limited by carrier migration, trapping, and recombination inside the bulks which account for most of the volume \[[@B27-nanomaterials-10-00378]\]. The nano form photocatalysts, with dimensions reaching tens of nanometers in scale, or even less than their corresponding Bohr radii, ought to possess enhanced photocatalytic quantum efficiency \[[@B28-nanomaterials-10-00378]\]. On account of the higher specific surface area and the smaller grain size, more surface catalytic sites and shorter distances from interior to surface of the material enable photo induced carriers to participate in surface redox reaction instead of loss in bulks. Similarly, designing and constructing nanostructures is the trend of enhancing sensing performance of semiconductor-based gas sensors.

To this end, researchers have synthesized nanomaterials by various methods and improved the efficiency of solar absorption and conversion efficiency of the photocatalysts by doping, constructing heterostructures and surface modification. Among them, carbon sphere template derived hollow nanostructure is one of the most promising methods to prepare high-efficiency photocatalysts and gas sensors due to some unique characteristics. First of all, the raw materials (any of the saccharides and some biomass) and products of template (carbon sphere) are environmentally friendly. Then, the surface functional groups adsorb metal ions uniformly and non-selectively, so we can realize doping, solid-solution, heterostructure, and surface modification easily by simply adjust the adsorption or annealing conditions. In view of these facts, we introduce a synthetic method that synthesizes a variety of multiple metal compound hollow spheres by using ions adsorption and templating approaches. This strategy could avoid the bulk form of the multiple metal compound in traditional synthesis process and tune the composition of different metals precisely. These multiple metal compound hollow spheres have shells in nanoscale and high specific surface areas, which bound to be helpful for photocatalysis, gas sensing, and other related reactions.

In this review, we will first give an overview on the synthesis of carbon sphere template and then summarized various synthetic routines toward carbon sphere template derived hollow nanostructures, including their advantages in synthesizing different types of nanostructure for photocatalysis (doping, solid-solution, heterostructure, surface modification). Secondarily, their valuable applications in gas sensing using the same idea as photocatalyst modification will be summarized and discussed. At the end of this review, challenges and outlooks in the field of carbon sphere template derived hollow nanostructure are highlighted.

2. Carbon Sphere Template---Overview of Synthesis {#sec2-nanomaterials-10-00378}
=================================================

Carbon spheres have been widely researched and applied to various fields---including batteries, photocatalysis, capacitors, and fuel cells---due to their easily available sources and facile synthesis. The last few decades have witnessed a rapid growth in sustainable energy field and this has led to the research of various application and approaches of carbon spheres, including carbonization routes \[[@B29-nanomaterials-10-00378]\], chemical vapor deposition (CVD) \[[@B30-nanomaterials-10-00378]\], ultrasonic-spray \[[@B31-nanomaterials-10-00378]\], and hydrothermal carbonization (HTC) \[[@B6-nanomaterials-10-00378],[@B32-nanomaterials-10-00378],[@B33-nanomaterials-10-00378]\]. Among these methods, hydrothermal carbonization is the one that aroused the greatest interest due to its facile procedure and mild experimental condition. Besides, carbon spheres obtained through HTC method have tunable diameters, great monodispersity, and excellent surface activities compared to carbon spheres synthesized by other procedures. Accordingly, HTC method is considered a perfect way to obtain carbon spheres as templates and assist the subsequent modification.

Wang et al. \[[@B34-nanomaterials-10-00378]\] successfully synthesized a novel monodispersed hard carbon spheres which is perfectly round with good surface condition and evenly distributed nanopores. In this experiment, carbon spheres were facilely prepared by two steps, including dehydration at low temperatures and carbonization at high temperatures of glucose. Sun et al. \[[@B32-nanomaterials-10-00378]\] put forward a simplified hydrothermal procedure to synthesize micro- or nanospheres. Carbon nano- and microspheres were synthesized directly using aqueous glucose solution as precursor by the method of hydrothermal synthesis at 160--180 °C. The growth model of carbon spheres is shown schematically in [Figure 1](#nanomaterials-10-00378-f001){ref-type="fig"}. The synthesis process is facile, and the as-prepared hard carbon spheres were tunable in diameters, crystallinity, chemical composition, with reactive surface and inherited functional groups of the precursor. Titirici et al. \[[@B35-nanomaterials-10-00378]\] reported a one-pot synthesis to obtain hollow spherical metal oxides such as Fe~2~O~3~, Ni~2~O~3~, Co~3~O~4~, CeO~2~, MgO, and CuO via a hydrothermal approach by directly adding glucose or sucrose as precursor and metal oxide precursors. It is to be observed that, during the synthesis procedure, the carbon spheres were also formed and serve as templates and this method is more simplified but it has no harmful effects for metal oxide hollow spheres. Although the hydrothermal carbonization (HTC) method for carbon spheres is mature and widely used, there exist some limitations that restrict the formation of relatively small size of carbon sphere. Tan et al. \[[@B36-nanomaterials-10-00378]\] finally overcome this barrier by varying parameters of hydrothermal carbonization process---including glucose concentration, pH value, and temperature---and synthesize small-sized carbon spheres (40 nm) for the first time.

A typical hydrothermal synthesis for carbon sphere template consists of 5g glucose dissolving in 30 ml water, sealing in a 50 mL autoclave and maintaining at 180 ℃ for 6 h. The as-prepared templates were isolated by several rinsing-centrifugation cycles until the solution is clear and oven-dried. Among some details of the experiment, we found the dispersion of the template can be controlled by trace amount of surfactant, solubility of glucose and quenching of the autoclave.

Besides, surface property of carbon spheres and precursors of carbon spheres have been widely studied in recent years. The surface of carbon spheres, especially those synthesized from hydrothermal reaction, possess high density of hydrophilic groups such as --OH and C=O groups, so that can absorb various of metal ions easily and uniformly without any further modification \[[@B37-nanomaterials-10-00378]\]. This is the critical superiority when carbon spheres are applied as templates. Moreover, many researchers are focusing on a wide range of source to obtain carbon spheres by hydrothermal reaction, including general monosaccharide (xylose \[[@B38-nanomaterials-10-00378]\], glucose \[[@B38-nanomaterials-10-00378]\]), disaccharides (sucrose \[[@B6-nanomaterials-10-00378],[@B38-nanomaterials-10-00378]\], lactose \[[@B39-nanomaterials-10-00378]\]), polysaccharides (starch \[[@B40-nanomaterials-10-00378],[@B41-nanomaterials-10-00378]\], cellulose \[[@B42-nanomaterials-10-00378]\]), and some biomasses \[[@B39-nanomaterials-10-00378]\]. The possible formation procedure is shown schematically in [Figure 2](#nanomaterials-10-00378-f002){ref-type="fig"}. These studies showed that all these sources could be applied to synthesize sphere-like carbon sphere-like structures which contained amounts of hydrophilic reactive functional group on the surface, but the qualities (such as morphology and dispersivity) of carbon spheres are better when saccharides are chosen as precursors due to the structural complexity of biomasses \[[@B39-nanomaterials-10-00378]\]. Despite all of this, using biomasses to synthesize carbon spheres will continue to be a hot spot because of its abundant resources, environmental friendliness, and consistency of sustainable development.

In addition, there are also some reports about sphere-like carbon with some changes of morphology, including mesoporous carbon, hollow carbon spheres, which can also be applied as templates \[[@B43-nanomaterials-10-00378],[@B44-nanomaterials-10-00378],[@B45-nanomaterials-10-00378]\]. Mesoporous and hollow carbon spheres are synthesized by a numerous methods, such as carbonization and a template procedure. Mesoporous hollow carbon spheres could be obtained through carbonization of polystyrene (PS) \[[@B43-nanomaterials-10-00378]\]. Carbon hollow spheres with tunable diameter and surface properties have studied and prepared with the use of templates such as silica spheres, some polymer spheres, metallic templates \[[@B44-nanomaterials-10-00378]\], and some other core templates \[[@B45-nanomaterials-10-00378]\]. There is still great necessity to deeply research the preparation of various carbon spheres (both morphology and property) to realize a synthesis method that starts with environmental-friendly materials and involves a facile synthesis process.

3. Carbon Sphere Template Derived Hollow Nanostructure: Advantages in Synthesizing Different Types of Nanostructures for Photocatalysis {#sec3-nanomaterials-10-00378}
=======================================================================================================================================

From recent studies, the nanoscale morphology could conducive to enhance the charge carriers' separation and transfer efficiency as well as raise the density of catalytic sites and it is one of the keys to improve photocatalytic performances \[[@B27-nanomaterials-10-00378],[@B28-nanomaterials-10-00378],[@B37-nanomaterials-10-00378]\]. However, for these traditional methods such as sol--gel and sintering methods, a precipitation or solid-state reaction process is essential to mix the different metal ions on molecular level. Resultantly, the large particle size and the aggregation phenomena are inevitable in multiple metal compounds \[[@B46-nanomaterials-10-00378]\]. Thus a general method for the synthesis of multiple metal compounds consists of doping, heterostructure, and surface modification strategies in nanoscale is essential in photocatalysis. Carbon sphere template derived hollow nanostructure is such a way to achieve the above strategies. Even controllable multi-layer hollow structures can be realized by different post-processing methods \[[@B47-nanomaterials-10-00378]\]. As shown in [Figure 3](#nanomaterials-10-00378-f003){ref-type="fig"}, it is the illustration of carbon sphere template derived hollow nanoheterostructure and controllable multilayer structure.

3.1. Doping {#sec3dot1-nanomaterials-10-00378}
-----------

Most metal oxide semiconductors with wide band gap could hardly respond to the visible light region \[[@B48-nanomaterials-10-00378]\], which limit their application in photocatalysis. Hence it is urgent to design semiconductor-based photocatalysts active both in UV and visible light region. Doping metal oxides (TiO~2~, ZnO, WO~3~, etc.), polymetallic oxides and nitrides \[[@B49-nanomaterials-10-00378]\] with non-metals (C, O, S, N, P, etc.) \[[@B48-nanomaterials-10-00378]\] or metals (Na, Mg, Fe, Lanthanide, etc.) \[[@B50-nanomaterials-10-00378]\] expand the effective absorption to visible light region to promote light harvesting and photocatalytic performance. One of many valid methods to design efficient photocatalysts which also can absorb visible light is creating impurity levels in band gap by doping \[[@B51-nanomaterials-10-00378]\]. We can achieve doping of many kinds of desired metals into oxides taking the characteristics of good dispersion of carbon sphere template and its uniformly and non-selectively adsorption of metal ions. By further regulating the experimental process, the doping of non-metallic elements can also be realized.

For instance, Song et al. \[[@B52-nanomaterials-10-00378]\] demonstrated that Fe doped contents can be precisely regulated by using this simple templating method, so that they acquired broader light absorption region. Fe doping introduced impurity levels in the forbidden band confirmed by DFT (density functional theory) calculation, which narrowed the band gap of WO~3~. Meanwhile, WO~3~ nanostructured photocatalysts with 5 at % Fe showed the best photocatalytic performance due to the low recombination and high transformation of the photo-generated carriers. Besides, Na-doped ZnO nanostructures have been firstly fabricated by ion adsorption and template method utilizing carbon spheres as templates \[[@B53-nanomaterials-10-00378]\]. Na and Zn elements cannot be precipitated simultaneously because their chemical activities in solution differ from each other. Instead of co-precipitation method, they gather the Zn and Na cations uniformly and simultaneously on the surface of carbon spheres ([Figure 4](#nanomaterials-10-00378-f004){ref-type="fig"}a). Engineering the Zn-doped contents can tune the work function of Na-doped ZnO from 4.48 eV to 6.19 eV, and fermi level get closer to the level of valence band by the increasing of Na doping concentration, which presented the success of a *p*-type doping effect ([Figure 4](#nanomaterials-10-00378-f004){ref-type="fig"}b). They have got Na-ZnO/Pt with 0.7 at % which presented the highest photocatalytic H~2~ generation rate and it was obviously superior to pure ZnO ([Figure 4](#nanomaterials-10-00378-f004){ref-type="fig"}c).

Rare earth metals also play a vital role in metal doped semiconductor-based photocatalysts. According to Chao et al. \[[@B54-nanomaterials-10-00378]\], Nd^3+^ led to defects in the lattice which were acted as electron traps, and also could band with non-bridging O^2−^ around the network structure. Nd^3+^ doping could make a red shift of absorption spectrum for TiO~2~. In another study \[[@B55-nanomaterials-10-00378]\], they used cerium instead of neodymium to dope into titania hollow spheres. Ce^4+^ ions could trap the excited electrons and then electrons would be transferred to adsorbed oxygen on the surface like the reaction

With the increase of Ce^4+^ doping content, the space charge layer would be thinner, which efficiently separates electron--hole pairs.

Among all the non-metals used as dopant materials by using carbon spheres templating, carbon doping is relatively common. Carbon spheres are used as hard template and also provide a source of carbon doping. Shi et al. reported C-doped titania nanostructures and its photocatalytic application in 2012 \[[@B56-nanomaterials-10-00378]\]. They presented the preparation of carbon doped TiO~2~ nanostructures with a hierarchical macroporous channel structure ([Figure 5](#nanomaterials-10-00378-f005){ref-type="fig"}a), which showed high potocatalytic degradation performance. In another work \[[@B57-nanomaterials-10-00378]\], they deduced the formation mechanism of hollow 3D network structure ([Figure 5](#nanomaterials-10-00378-f005){ref-type="fig"}b), because the surface of carbon spheres was hydrophilic. Carbon doping narrowed the band gap of titania, and hollow 3D structure offered a pathway for guest molecules and enhanced the light harvesting. Recently, Shi's group \[[@B58-nanomaterials-10-00378]\] realized C~3~N~4~ decorated carbon-doped TiO~2~ by in situ growth ([Figure 5](#nanomaterials-10-00378-f005){ref-type="fig"}c). C doping influenced the energy band structure of TiO~2~ to enhance photocatalytic activity for application in hydrogen generation under simulated sunlight. Except carbon doping, there are a few works on non-metal doped semicondutor-based photocatalysis in hollow nanostructure, such as Br-doped TiO~2~ \[[@B59-nanomaterials-10-00378]\].

In addition to being visible-light absorption centers, dopant also could reduce recombination losses in photocatalyst by trapping photo-generated carriers. Reciprocally, it enhanced the carriers separation to obtain the superior photocatalytic performance. The non-selectively adsorption of carbon sphere template provides a good condition for various doping. For instance, Li et al. \[[@B60-nanomaterials-10-00378]\] described that Fe-doped LaTiO~2~N nanostructures exhibited high efficiency, because doping can match the level of conduction band between cocatalysts and LaTiO~2~N hollow nanostructures by creating empty mid-gap states in Fe doped LaTiO~2~N. As shown in [Figure 6](#nanomaterials-10-00378-f006){ref-type="fig"}a, Fe dopants created a defect level lower than the level of conduction band both of LaTiO~2~N and CoO*~x~*, so that the photo-generated electrons could be gathered to CoO*~x~* nanoparticles. As a result, the sample with 1.5% Fe doping exhibited quantum efficiency as high as 55% for O~2~ evolution which was fairly higher than other LaTiO~2~N system ([Figure 6](#nanomaterials-10-00378-f006){ref-type="fig"}b). Besides, dopant also can reduce the defect sites, where are electron--hole recombination's sites. Gao et al. \[[@B61-nanomaterials-10-00378]\] found that Mg dopants could not create new trapping states in TiO~2~ because it does not have d orbit, but the intrinsic defect states like oxygen vacancy (*V~o~*) could be suppressed by Mg doping ([Figure 7](#nanomaterials-10-00378-f007){ref-type="fig"}a). Moreover, the 2p orbit of Mg dopant apart from the level of conduction and valence band of TiO~2~ could change the level of defect states by hybridizing the oxygen vacancy in titania ([Figure 7](#nanomaterials-10-00378-f007){ref-type="fig"}b). Besides, as a narrow band-gap semiconductor, Ta~3~N~5~ also has numerous photo-generated carrier recombination centers, which seriously impairs its photocatalytic activity. Recently, Xiao et al. \[[@B62-nanomaterials-10-00378]\] prepared Mg-doped Ta~3~N~5~ hollow spheres using carbon spheres templating. Mg ions doped into Ta~3~N~5~ could not only increase the charge mobility but also tune the electronic structure to promote the charge transportation. From the result of Mott--Schottky measurement ([Figure 7](#nanomaterials-10-00378-f007){ref-type="fig"}c), Mg-Ta~3~N~5~ had a higher electron density. Theoretically, Mg ions acted as an electron acceptor in Ta~3~N~5~ photocatalysts. Mg doping was relatively efficient strategy, its photocatalytic hydrogen production is about 7.6-times that of prinstine Ta~3~N~5~ ([Figure 7](#nanomaterials-10-00378-f007){ref-type="fig"}d).

Researchers have successfully achieved the doping of different elements in various materials by using carbon sphere template method. According to the results, the distribution of doping elements is uniform and there is no phase separation. For some doping systems that cannot be achieved by other preparation methods, we can try to achieve it by the non-selective adsorption of carbon sphere templates. This also provides ideas for other systems such as single atomic catalysis. Different kinds of salts can be used to make the expected elements adsorb and anchor on the surface of the template, and metal particles with good dispersion may be obtained through subsequent treatment.

3.2. Solid Solution {#sec3dot2-nanomaterials-10-00378}
-------------------

The bandgap engineering of a semiconductor is very important for its application in various aspects. It not only determines the optical absorption edge and emission wavelength of the material, but also closely related to the electrical conductivity \[[@B63-nanomaterials-10-00378]\]. However, it is difficult to find some semiconductors in nature whose bandgaps fit the requirements of various applications precisely, and that makes bandgap engineering an indispensable study. In order to tailor the bandgap and optoelectronic property of semiconductors, scientists have come up with two main solutions, including doping and forming solid solutions ([Figure 8](#nanomaterials-10-00378-f008){ref-type="fig"}) \[[@B64-nanomaterials-10-00378]\]. The doping method has been described above. Forming solid solutions is to synthesize two or more different semiconductors (with similar crystal or electronic structure) into one material, and the bandgap-controllable solid solutions can be obtained by fine-tuning the content of different components. When applied to photocatalysis, the band gap is expected to be quite narrow while satisfying the potential of the catalytic reaction. Similar to the strategy of doping in previous section, carbon sphere template's uniform and non-selective adsorption of metal ions also enables the synthesis of solid solution hollow nanostructure. By precisely controlling the precursor concentration, a broad solid solubility can be achieved.

(Ga~1-*x*~Zn*~x~*) (N~1-*x*~O*~x~*) is formed by GaN and ZnO. Unlike a solid solution synthesized by a wide and a narrow band semiconductor, GaN and ZnO both have wide bandgaps, while their solid solution has a narrow bandgap about 2.58 eV when the content of ZnO is 13.3% \[[@B65-nanomaterials-10-00378]\]. It is calculated that the VBM (valence band maximum) is composed of Zn 3d orbitals and *N* 2p orbitals, and the repulsion of electrons of Zn 3d and *N* 2p result in the narrowing of the band gap \[[@B66-nanomaterials-10-00378]\], which makes the material more suitable for photocatalysis than sole GaN and ZnO. The water-splitting quantum yield of the bulk (Ga~1-*x*~Zn*~x~*)(N~1-*x*~O*~x~*) is limited by carrier migration, trapping and recombination. Maeda et al. \[[@B67-nanomaterials-10-00378]\] enhanced the quantum efficiency to 5.9% at 420--440 nm by surface modification, optimizing annealing temperature and composition *x* of bulk (Ga~1−*x*~Zn*~x~*)(N~1−*x*~O*~x~*). Many scientists have improved the overall conversion efficiency of the system by preparing nanomorphological materials. Reinert et al. \[[@B68-nanomaterials-10-00378]\] obtained nanorods arrays with diameter of about 100 nm. Their Ga~2~O~3~(ZnO)~16~ precursor was heat-treated and cooled under NH~3~ flow. By reducing the synthesis temperature to 850 °C, the volatilization of Zn was also greatly reduced, thus increasing the *x* value from \<0.42 to 0.55 \[[@B65-nanomaterials-10-00378]\], and reducing the band gap to 2.53 eV. Li et al. \[[@B69-nanomaterials-10-00378]\] synthesized (Ga~1−*x*~Zn*~x~*)(N~1−*x*~O*~x~*) nano-hollow spheres by ion adsorption and templating. They used carbon spheres as templates, DMF as solvent, supplemented with the subsequent nitridation, and obtained various composition of (Ga~1−*x*~Zn*~x~*)(N~1−*x*~O*~x~*) by adjusting the ratio of the Zn source to the Ga source, tuning the composition of ZnO to the full range from 0.18 to 0.95. The magnified TEM image ([Figure 9](#nanomaterials-10-00378-f009){ref-type="fig"}a) shows the nano-hollow-spheres, whose diameter are approximately 100--120 nm and the shell of the sphere is about 7 nm thick. [Figure 9](#nanomaterials-10-00378-f009){ref-type="fig"}c indicates that using this new synth etic method, the narrowing of the bandgap is related to the mutual approachment of both VBM and CBM (conduction band minimum). The nitridation temperature was only 600 °C attributing to the the nanoscale hollow structures, much lower than that of bulk form which is approximately 900 °C \[[@B70-nanomaterials-10-00378]\], thus it reduces the volatilization of Zn. This nanoscale structure also decreases the carrier diffusion distances and increases the number of reaction sites, enhancing the quantum efficiency to 17.3% (400 nm), which was about 3 times higher than bulk (Ga~0.82~Zn~0.18~)(N~0.82~O~0.18~) \[[@B67-nanomaterials-10-00378]\].

A similar situation exists in some other solid solution systems. Zn*~x~*Cd~1-*x*~S is a solid solution composed of CdS and ZnS, which not only has tunable band gap, but also has better photocorrosion resistance and higher photocatalytic activity than pure CdS \[[@B71-nanomaterials-10-00378],[@B72-nanomaterials-10-00378]\]. Gholipour et al. \[[@B73-nanomaterials-10-00378]\] synthesized Zn*~x~*Cd~1-*x*~S hollow spheres by a solvothermal method, using glycerin to obtain carbon microspheres \[[@B74-nanomaterials-10-00378]\], which contains large amount of OH radicals that can adsorb Zn^2+^ and Cd^2+^. After centrifugated, calcinated and calcinated in H~2~S/Ar flow, the Zn*~x~*Cd~1-*x*~S hollow spheres can finally be obtained. The value of x can be tuned by adjusting the ratio of zinc source to cadmium source.

The nanostructure of Zn*~x~*Cd~1-*x*~S is hollow sphere with an average diameter of 500 nm ([Figure 10](#nanomaterials-10-00378-f010){ref-type="fig"}a,b). With the increase of Cd content, the absorption edge moves towards longer wavelength ([Figure 10](#nanomaterials-10-00378-f010){ref-type="fig"}c), indicating the decrease of bandgap. At the same time, the XRD (X-ray diffraction) peak of the samples gradually shifted to lower angle ([Figure 10](#nanomaterials-10-00378-f010){ref-type="fig"}d), accounting for the transformation from hexagonal ZnS to hexagonal wurtzite CdS. The hydrogen evolution they received is as high as 12 mmol h^−1^ g^−1^ under solar irradiation using MoS~2~ as cocatalyst. The calculated quantum efficiencies (QE) reached to 46.6% at 400 nm, which was among the highest QE in this system.

So far, there are few solid solution systems realized by carbon sphere template method. By adjusting the precursor and subsequent treatment, this method may be able to achieve more solid solution hollow nanostructures.

3.3. Heterostructure {#sec3dot3-nanomaterials-10-00378}
--------------------

It is hardly for individual semiconductor materials to satisfy fundamental requirements of highly efficient photocatalysts, such as suitable bandgap for effective sun light absorption, proper charge separation, high carrier mobility and fast kinetics for surface reaction \[[@B75-nanomaterials-10-00378],[@B76-nanomaterials-10-00378]\]. Introducing heterojunction comes to be a potential strategy to meet these critical requirements simultaneously by combining the advantages of two or more semiconductors. A conventional heterojunction is established by coupling two semiconductors having suitable structures of energy band directly. Heterostructured hollow photocatalysts have received growing research attention by cause of their unusual advantages such as ultrahigh sunlight absorption, extremely large surface area and short carrier transfer distance in recent year \[[@B76-nanomaterials-10-00378],[@B77-nanomaterials-10-00378]\]. So far, heterostructured hollow photocatalysts have demonstrated great application potential in varied photocatalytic fields \[[@B49-nanomaterials-10-00378],[@B78-nanomaterials-10-00378]\]. Due to the good adsorption capacity of carbon sphere template, we are able to obtain hollow nano heterostructures by multiple adsorption and different annealing conditions.

Semiconductor-based photocatalysts applied in water splitting are identified as the most economic and environmentally friendly material systems for hydrogen production \[[@B79-nanomaterials-10-00378]\]. In recent years, a great deal of previous research spotlighted on water splitting based on advanced heterostructured hollow photocatalysts.

For instance, Song et al. \[[@B80-nanomaterials-10-00378]\] demonstrated the superior photocatalytic H~2~ evolution activity of ZnFe~2~O~4~/ZnO hollow nanoheterostuctures by a facile hard-templating approach. The nanoheterostuctures of ZnFe~2~O~4~/ZnO, which are about 15 nm in size, are homogeneously distributed in the hollow sphere shell. The champion sample without the help of co-catalysts exhibits an outstanding H~2~ evolution rate of 2.15 mmol h^−1^ g^−1^ when irradiated by visible light. The corresponding quantum efficiency reaching 1.61%, which is 7.6 times higher than that of bare hollow ZnFe~2~O~4~ photocatalysts. ZnO forms a type-II heterojunction with ZnFe~2~O~4~ in the sphere shell ([Figure 11](#nanomaterials-10-00378-f011){ref-type="fig"}) which confirmed by the combination investigation of XPS (X-ray photoelectron spectroscopy) technic as well as UV--vis diffuse reflectance spectroscopy. The photogenerated electrons and holes will be separated into the conduction band of ZnO and valence band of ZnFe~2~O~4~ by the built-in electric field, respectively, thereby minimizing the recombination and boosting the photocatalytic H~2~ generation performance of samples. Meanwhile, Li et al. \[[@B81-nanomaterials-10-00378]\] have reported a high-crystallinity g-C~3~N~4~/TiO~2~ hollowsphere nanoheterojunction photocatalyst with large surface area through a carbon sphere templating method. By carefully tuning the ratio of precursors, the optimum g-C~3~N~4~/TiO~2~ photocatalyst obtain a 5.5-fold enhancement in visible-light-driven hydrogen generation rate, reaching almost 470 μmol g^−1^ h^−1^. The improvement in photocatalytic performance primarily owes to the establishment of heterojunctions which accelerating carrier's separation efficiently confirmed by PL spectrum and electrochemical independence spectroscopy. While conventional heterojunctions are generally in form of crystalline/crystalline contact, Lou et al. \[[@B82-nanomaterials-10-00378]\] have investigated a novel type of crystalline/amorphous heterostructure. A crystalline Cu~2~O/amorphous Ta~2~O~5~ heterostructure fabricated by a two-step ion absorption approach based on carbon spheres template. Such heterostructures were found to possess the capacity for splitting water into H~2~ and O~2~ driven by visible light without using sacrificial agent. Theoretical calculation shows the existence of hole trap states in the crystalline/crystalline interface cause by lattice and electron mismatch, which does not exist at the crystal/amorphous interface ([Figure 12](#nanomaterials-10-00378-f012){ref-type="fig"}). Moreover, the type-II heterojunction of crystalline Cu~2~O/amorphous Ta~2~O~5~ greatly promotes the separation of photo-induced charges to perform effective overall water splitting.

In addition, other research groups also have reported hollow heterojunction photocatalysts with high performance. Waqas et al. \[[@B83-nanomaterials-10-00378]\] prepared hollow sphere TiO~2~/Fe~2~TiO~5~ heterojunction photocatalyst through a simple two-step templating method for high efficient solar water oxidation. The oxygen evolution reaction rate of the champion sample with 35% Fe reached 375 μmol h^−1^ g^−1^ benefited from the desirable energy band alignment of TiO~2~/Fe~2~TiO~5~ heterojunction, which improved carrier separation in these photocatalysts. In another work, heterostructured ZnFe~2~O~4~/ZnSe hollow sphere photocatalysts which were synthesized through two-step carbon templating approach used in visible-light-driven water splitting \[[@B84-nanomaterials-10-00378]\]. Heterostructured ZnSe photocatalysts with suitable shell thickness generated a large amount of H~2~ of 16.9 mmol g^−1^ in 6 h, owing to the effective charge separation and accelerated carrier transfer.

Hollow nanoheterostructured photocatalysts possess extremely large surface area, high catalytic activity and carrier separation efficiency, thus being suitable for application of pollutant degradation \[[@B49-nanomaterials-10-00378],[@B75-nanomaterials-10-00378],[@B77-nanomaterials-10-00378],[@B85-nanomaterials-10-00378]\].

In 2014, Li et al. \[[@B86-nanomaterials-10-00378]\] have pioneered a simple and universal method for fabricating a hybrid hollow nanoheterostructured photocatalyst with ultrathin shell. Taking the TiO~2~/SnO~2~ hollow sphere photocatalyst as a typical example, they mixed 0.5 g of carbon spheres and a proper amount of C~16~H~36~O~4~Ti and SnCl~2~·2H~2~O together and stirred for 24 h, followed by rinsing and drying in an oven at 80 °C for 6 h. The TiO~2~/SnO~2~ hybrid nanostructured hollow spheres finally obtained by calcination have 3--10 nm small grain size and ultrahigh surface area of 300 m^2^ g^−1^. Compared to single TiO~2~ and SnO~2~ hollow nanostructured photocatalysts, the TiO~2~/SnO~2~ hybrid hollow nanostructured photocatalyst shows a superior RhB dye photodegradation activity, which is profited from the built-in electric field induced by TiO~2~/SnO~2~ heterojunction as well as the short carrier diffusion length in TiO~2~/SnO~2~ nanocrystal ([Figure 13](#nanomaterials-10-00378-f013){ref-type="fig"}). Adopting a similar strategy, Lou et al. \[[@B87-nanomaterials-10-00378]\] have also successfully prepared a hollow Fe~2~TiO~5~/TiO~2~ nanoheterostructure to enhance the photocatalytic performance of TiO~2~-based photocatalysts driven by visible light. The favorable energy band alignment of Fe~2~TiO~5~/TiO~2~ heterojunction suppressed the carrier recombination significantly. As a result, the optimum nanoheterostructured photocatalyst exhibited a 3-times higher visible-light photocatalytic-degradation activity towards RhB compared to that of commercial P25 photocatalyst.

Diversification of structural morphology makes hollow sphere photocatalysts more attractive. Ang et al. \[[@B85-nanomaterials-10-00378]\] have reported multi-dimensional hierarchical hollow heterojunctioned CuO/TiO~2~ spheres with TiO~2~ thorns grown on the surface of CuO hollow spheres by a carbon spheres assisted template method ([Figure 14](#nanomaterials-10-00378-f014){ref-type="fig"}a,b). The hierarchical TiO~2~ thorns acted as water channels generating a mass of reactive oxygen species for pollutant degradation. The multi-dimensional CuO/TiO~2~ spheres show an excellent photodegradation activity in comparison to P25 thanks to the effective carrier separation and migration origin from the establishment of CuO/TiO~2~ heterojunction. Liu et al. \[[@B88-nanomaterials-10-00378]\] have successfully used a microwave-assistant carbon sphere templating method to synthesize hollow nest-like *γ*-Fe~2~O~3~/ZnO photocatalysts, which ZnO nanosheets were loaded on the shell of g-Fe~2~O~3~ hollow spheres ([Figure 14](#nanomaterials-10-00378-f014){ref-type="fig"}c,d). The large surface area and effective restraint of carrier recombination of g-Fe~2~O~3~/ZnO result in an enhanced photocatalytic activity compared with bare ZnO photocatalysts.

Other type-II hollow heterostructured photocatalysts derived from carbon sphere template such as CeO~2~/TiO~2~ \[[@B89-nanomaterials-10-00378]\], WO~3~/TiO~2~ \[[@B90-nanomaterials-10-00378]\], ZnO/CuO \[[@B91-nanomaterials-10-00378]\], ZnO/SnO~2~ \[[@B92-nanomaterials-10-00378]\], and ZnO/ZnS \[[@B93-nanomaterials-10-00378]\] also showed enhanced photocatalytic pollutant degradation performance by the promotion of heterojunction.

Nanoheterostructure is one of the most facilely realized structures by carbon sphere template method. One-step adsorption by the carbon sphere template can realize heterostructure on the same spherical shell, and multi-step adsorption can realize hollow spherical nanostructures with core--shell distribution or multilayer structure. Notably, as powder photocatalysts, recycling is a very important issue. Generally, we build a heterostructure with magnetic materials to achieve magnetic recycling. However, magnetic materials generally have low photocatalytic activity and light blocking, which will reduce the efficiency of light utilization. By carbon sphere template method, the magnetic materials may be confined in the hollow nanospheres of photocatalyst by the method of multi-step adsorption, so as to realize the light utilization efficiency and recyclability.

3.4. Surface Modification {#sec3dot4-nanomaterials-10-00378}
-------------------------

For photocatalysis, the more electron--hole pairs are photogenerated and come into play, the higher the efficiency will be. However, the recombination is proven to harmfully impede the process of water-splitting or degradation resulting in a low efficiency \[[@B27-nanomaterials-10-00378],[@B37-nanomaterials-10-00378],[@B82-nanomaterials-10-00378]\]. Hollow structures can shorten the transport distance of carries from bulk to their proper catalytic sites on the surface, which suppress bulk recombination tremendously \[[@B37-nanomaterials-10-00378],[@B77-nanomaterials-10-00378]\]. However, a majority of surface defects remain there and behave as another kind of recombination centers \[[@B94-nanomaterials-10-00378]\]. Meanwhile the extra electronic and optical states may have an influence on electronic structure or band structure \[[@B95-nanomaterials-10-00378]\]. Surface modification is the most effective measure to suppress surface recombination and increase active sites. Carbon sphere templates can absorb precious metals uniformly in solution, and also can be used as good skeleton support in subsequent treatment. The carbon sphere template derived ultra-thin hollow nanostructure also provides favorable conditions for the subsequent surface modification. Furthermore, combining surface modification and hollow structure will endow photocatalysts with both higher activity and better stability.

The introduction of disorder at the surface of photocatalysts is a common method of surface modification. It has been revealed that lattice disorder in semiconductors could yield band tail states. It would dominate the optical excitation and relaxtion, and provide intended trapping sites for photo-generated carriers to avoid rapid recombination \[[@B96-nanomaterials-10-00378],[@B97-nanomaterials-10-00378]\]. Chen et al. \[[@B96-nanomaterials-10-00378]\] prepared TiO~2~ nanocrystals with disordered surface layers via hydrogenation and found that it could help harvest infrared optical photons and contribute to organic molecules photo-oxidation and H~2~ evolution. Li et al. \[[@B95-nanomaterials-10-00378]\] reported a surface-reconstruced hollow LaTiO~2~N nanostructure with significantly improved photocatalytic activity ([Figure 15](#nanomaterials-10-00378-f015){ref-type="fig"}). The ultrathin hollow LaTiO~2~N spheres were firstly synthesized by utilizing carbon spheres as hard templates. Then H~2~ treatment was carried not only to load the cocatalyst Pt but also to modify the surface of LaTiO~2~N spheres. Pt/H-LTON achieved a remarkably improved H~2~ evolution rate (up to 192 μmol h^−1^, compared to 91 μmol h^−1^ of Pt/LTON) and stability. Interestingly, the contrast sample with extra N~2~ annealing, which maintained the presence of Ti^3+^ ions but removed the disordered surface even exhibited worse photocatalytic performance than Pt/LTON. It indicated that the excellent photocatalytic capacity for water splitting was a consequence of the disordered surface rather than the induced Ti^3+^ ions. Introducing H atom can passivate surface defects, thus avoiding a majority of surface recombination of photo-induced carriers \[[@B94-nanomaterials-10-00378],[@B95-nanomaterials-10-00378]\]. Therefore, surface disordering functions as a complementary strategy for improving photocatalytic activity combined with hollow structures.

Oxygen vacancies are also proved to strongly affect photocatalytic activity of metal oxides-based photocatalysts \[[@B98-nanomaterials-10-00378]\]. Black titanium oxide is a typical example, in which electrons transition occurs between levels of valence band of the photocatalyst and the introduced oxygen vacancy states under visible radiation \[[@B98-nanomaterials-10-00378],[@B99-nanomaterials-10-00378]\]. Recently, Song et al. \[[@B100-nanomaterials-10-00378]\] successfully prepared black titanium oxide hollow nanospheres with ultrathin shells for more effective solar-driven water splitting ([Figure 16](#nanomaterials-10-00378-f016){ref-type="fig"}). The high quality TiO~2~ possessed a high specific surface area of 168.8 m^2^ g^−1^ and was obtained by a conventional carbon sphere templating method combined with subsequent Al reduction. This black TiO~2~ nanostructure exhibited a much higher photocatalytic H~2~ evolution rate (56.7 mmol h^−1^ g^−1^), which was well above that of the as-prepared one (22.9 mmol h^−1^ g^−1^) when using xenon lamp as irradiation source. It was found that Al reduction introduced masses of oxygen vacancies into TiO~2~ which can act as donors and accelerate the separation and transportation of the photogenerated electron--hole pairs.

Besides, cocatalysts can help lower energy barriers, enhance photo-generated charge separation and provide reaction sites \[[@B101-nanomaterials-10-00378]\]. Different cocatalysts are designed to facilitate the oxidation or reduction process on the surface respectively \[[@B102-nanomaterials-10-00378]\]. Template method makes it easy to load related cocatalysts to the specified spots of photocatalysts. For example, Li et al. \[[@B102-nanomaterials-10-00378]\] designed Pt\@TiO~2~\@MnOx hollow spheres to improve the photo-oxidation of water and benzyl alcohol. Xiao et al. \[[@B62-nanomaterials-10-00378]\] reported that the Ta~3~N~5~ hollow spheres with Pt/CoOx dual cocatalysts exhibited better photocatalytic ability of water splitting compared with those only with Pt cocatalyst. Hollow TiO~2~ modified with spatially isolated Au and CoO dual cocatalysts for CO~2~ photoreduction was designed by Zhu et al. ([Figure 17](#nanomaterials-10-00378-f017){ref-type="fig"}) \[[@B103-nanomaterials-10-00378]\]. CoO was formed on the inner surface of carbon spheres by ions absorption, and then Au was decorated on the external surface by Au ions reduction. The optimal formation rate of CH~4~ from CO~2~ reduction of Au~2.0~\@THS\@CoO was nearly 60 times as high as that of TiO~2~ hollow nanospheres (THS), while the activity of THS with Au and CoO nanoparticles randomly deposited was not so good. There is convincing evidence that Au and CoO are the suitable co-catalysts for photo-generated electrons and holes respectively so that carriers can be separated effectively on the inner or outer surfaces of the hollow nanostructure. Carbon templating is a convenient way of designing cocatalyst loading.

Furthermore, plasmonic metal nanocrystals have been intensively investigated recently on account of its unique optical and electronic properties. Gold (Au) and silver (Ag) can work as cocatalysts as well as light sensitizers in aspect of photocatalysis. Wang et al. \[[@B104-nanomaterials-10-00378]\] synthesized yolk--shell Au\@TiO~2~ nanostructure by employing carbon spheres as templates ([Figure 18](#nanomaterials-10-00378-f018){ref-type="fig"}). Core--shell Au\@C was fabricated through hydrolysis and then it worked as a template to form yolk--shell Au\@TiO~2~ (Au\@TiO~2~-YS). The diameter of Au\@TiO~2~-YS was about 350 nm with the Au core 70--90 nm or so. Evidently, this morphology brought a much larger BET (Brunauer--Emmett--Teller) surface area reaching 128.9 m^2^/g and a higher content of mesoporous particles than core--shell Au\@TiO~2~. Owing to plasmonic effects, Au\@TiO~2~-YS had broader light absorption extended to about 570 nm. It was found to be able to degrade the gaseous toluene more efficiently than the core--shell structure, almost 1.63 times higher. Obviously, the large surface area and abundant mesoporous channels induced by the yolk--shell structure make it easy to absorb more VOCs (Volatile Organic Compounds) and proceed the degradation. In addition, thin shells are also beneficial for photo-generated carriers to separate and migrate and unique cavities increase light reflection and refraction, too, thus enhancing the LSPR (Localized Surface Plasmon Resonance) effect of Au.

In addition, passivation layers can also modify the surface of hollow structure. Xiao et al. \[[@B62-nanomaterials-10-00378]\] demonstrated that MgO nano-layer as passivation layer seemed to be an effective strategy for Mg-doped Ta~3~N~5~ hollow spheres ([Figure 19](#nanomaterials-10-00378-f019){ref-type="fig"}). The Mg-doped Ta~2~O~5~ precursor fabricated with the aid of carbon spheres templating, and subsequently it was well wrapped in-situ by a thin layer of MgO even less than 5 nm. The particle size of Pt further dercreased from 2.04 nm to 1.33 nm along with the deposition of MgO. The increased ratio of hydrogen generation for MgO modification is 17.3 compared to the bulk Ta~3~N~5~, mainly due to the efficient charge transfer and passivation of surface defects. It should be noted that excessive MgO may adversely affect the charge transfer between Ta~3~N~5~ and cocatalysts instead since MgO is known as a insulator. Therefore, it is necessary to manage the thickness of the passivation layer by controlling the parameters of ion absorption.

Surface modification is not unique to the carbon sphere template method, but the adsorption characteristics of carbon sphere can well realize the delocalization of different co-catalysts. The carbon in the template can also acts as reducing agent. Under different post-treated atmosphere, it can play a role not only as a template. The hollow nanostructures with controllable shell thickness prepared by carbon sphere template method also provide convenience for many subsequent processing. In photocatalysis, the carrier migration distance is a very important factor. The thin shell prepared by carbon sphere template with subsequent surface treatment can greatly improve the efficiency of photocatalyst carrier utilization.

A summary of the recent carbon sphere template derived hollow nanostructure photocatalysts is presented in [Table 1](#nanomaterials-10-00378-t001){ref-type="table"}.

4. Carbon Sphere Template Derived Hollow Nanostructure for Gas Sensing {#sec4-nanomaterials-10-00378}
======================================================================

Hollow nanostructure also has widely applied in gas sensing since it possesses ultrahigh specific area which can provide rich active sites for gas adsorption and diffusion, further promoting gas-sensing performance. Moreover, the porous structures resulting in high surface permeability also allows more gas exposure and makes gas sensing easier \[[@B105-nanomaterials-10-00378],[@B106-nanomaterials-10-00378],[@B107-nanomaterials-10-00378]\]. Inspired by carbon sphere templating methods in photocatalysis, researchers have successfully implemented the modification strategies into gas sensing in view of carbon spheres templated hollow nanostructure with adjustable composition, thickness, surface, and interface \[[@B108-nanomaterials-10-00378],[@B109-nanomaterials-10-00378],[@B110-nanomaterials-10-00378]\].

For instance, Zhang et al. \[[@B111-nanomaterials-10-00378]\] firstly designed porous Co~3~O~4~/Ta~2~O~5~ heterojunction hollow nanospheres. They prepared ultrathin Ta~2~O~5~ hollow shell (shell thickness \~5 nm) attached with numerous Co~3~O~4~ nanoparticles by adsorbing Co ions onto Ta^5+^/C template spheres ([Figure 20](#nanomaterials-10-00378-f020){ref-type="fig"}a--d). [Figure 20](#nanomaterials-10-00378-f020){ref-type="fig"}e displayed that the gas sensor owned a good linear relationship of current vs. voltage between the sensing material and the electrode, ensuring that measured electrical signals were due to the gas-sensing performance rather than the contact resistance of the sensing material and the electrode. The gas sensor revealed splendid selectivity and reliable long stability to ethanol at room temperature ([Figure 20](#nanomaterials-10-00378-f020){ref-type="fig"}h--k), which was attributed to two reasons: (1) the supporting effect of Ta~2~O~5~ hollow spheres hindered the agglomeration of Co~3~O~4~ particles and guaranteed larger BET area; (2) the formation of heterojunction resulted to widen the electronic depletion layer.

Furthermore, Zhang et al. \[[@B112-nanomaterials-10-00378]\] also synthesized WO~3~ mesoporous hollow nanospheres doped with Fe with a series of concentrations (0--5.2% by molar ratio) through a carbon colloidal nanosphere templating method, electrostatic adsorption of metal ions, as well as post-annealing treatment. This hollow structure showed tiny size and ultrahigh BET area. Gas sensor based on hollow nanostructured semiconductors finally realized outstanding performance applied for ppb-level NO~2~ detection at lower working temperature (100--140 °C) as exhibited in [Figure 21](#nanomaterials-10-00378-f021){ref-type="fig"}. According to the results of XPS, the enhancement of NO~2~ detecting performance ascribed to rich oxygen vacancies and surface chemical states altered by Fe dopants. What is worth mentioning is that the excellent detection limitation can meet the needs of atmospheric monitoring and exclusive detecting at the same time.

Zhang et al. \[[@B113-nanomaterials-10-00378]\] studied hollow carbon spheres of which Co~3~O~4~ nanowires assembled on the surface (Co~3~O~4~ NWs-HCSs) by hydrothermal method together with subsequent heat treatment for acetone gas sensing ([Figure 22](#nanomaterials-10-00378-f022){ref-type="fig"}a). Obviously, Co~3~O~4~ NWs-HCSs behaved talented selectivity for acetone, and whose response increased to 23 at 150 °C, even possessed high response at lower temperature of 75 °C, approaching room temperature.

Most researchers tend to study low temperature (even room temperature) and low concentration gas sensing taking the advantages of hollow structure, however they lacked research on humidity sensitivity. Notably, Mutuma et al. \[[@B114-nanomaterials-10-00378]\] reported that pristine hollow carbon spheres (HCSs), HCS/PVP (polyvinyl pyrrolidone) composite and annealed HCSs as ammonia sensors in damp conditions. The authors used a surfactant dispersion method to fabricate the HCSs and HCS/PVP. HCSs sensor should have responded in a high relative humidity (10--97% RH) owing to the presence of amorphous domains and oxygenated groups while high concentration of water molecules inhibited ammonia adsorption sites ([Figure 23](#nanomaterials-10-00378-f023){ref-type="fig"}a). After adding PVP, HCSs still behaved obvious conductivity attenuation under high humidity resulting from polymer swelling and plasticization ([Figure 23](#nanomaterials-10-00378-f023){ref-type="fig"}b). After subsequent annealing, the annealed HCSs obtained a great response to 74--295 ppm NH~3~ over a broad RH range ([Figure 23](#nanomaterials-10-00378-f023){ref-type="fig"}c,h,i), decreasing the dependence on RH and raising surface area. This study provided insights into a step forward to modify the HCSs sensor in high humidity.

The above research presents several promising strategies to enhance gas-sensing performance through carbon sphere derived hollow nanostructure. Based on these studies, after further optimization on structure and process conditions, as well as material systems innovation, carbon sphere template derived hollow nanostructures would be promising in low temperature especially room temperature and ppb-level gas detection in high relative humidity environment, making it possible to apply in exhaled breath detecting in the future. A summary of the recent carbon sphere template derived hollow nanostructure gas sensors is presented in [Table 2](#nanomaterials-10-00378-t002){ref-type="table"}. Furthermore, hollow structures also have plenty of applications in the fields in energy storage \[[@B115-nanomaterials-10-00378],[@B116-nanomaterials-10-00378]\].

5. Conclusion and Outlook {#sec5-nanomaterials-10-00378}
=========================

In summary, carbon sphere template derived hollow nanostructure has attracted considerable attention and achieved great progress in the fields of photocatalysis, gas sensing, etc. Among template methods, the use of highly hazardous, complex, inefficient, and costly fluoride-containing or strong acids and bases to etch the sacrificial templates limits their large-scale production and practical application. For these reasons, developing green, facile, and efficient strategies especially carbon sphere template derived hollow nanostructures with better photocatalysis and gas sensing performance is highly desirable and meaningful.

After tremendous efforts, the family of carbon sphere template derived hollow nanostructures have been broadened from monometal oxides to multimetal compounds. More importantly, doping, solid solution, heterostructure, and surface modification strategies have been successfully realized in carbon sphere template derived hollow nanostructures. These successful attempts are due to the unique characteristics of carbon sphere templates like the whole synthesis process is totally green and the surface radicals adsorb metal ions uniformly and non-selectively. This strategy is of great help to the three steps of photocatalytic process which enhancing light absorption, promoting carrier separation and benefiting surface redox reaction. This review summarized the recent development of carbon sphere template derived hollow nanostructures in photocatalysis. We summarize various synthetic routines of carbon spheres and carbon sphere template derived hollow nanostructures and highlight the mechanism for photocatalytic performance enhancement. The strategy has been also successfully applied in the field of gas sensing thus we present a summary of the recent progress in the development of carbon sphere template derived hollow nanostructures for gas sensing and related applications as well.

Despite significant progress in synthesis and effective property tuning of carbon sphere template derived hollow nanostructures, there are still some challenges and opportunities. For example, there are still many opportunities for research in the preparation of other types of fully adjustable solid solutions and tailoring bandgaps in most material systems. More systematic studies are needed to study the distribution of the minority atoms on the surface, such as whether the atomic dispersion can be achieved and applied to other reactions like photocatalytic CO~2~ reduction or nitrogen fixation. It is important to realize synthesis of configurationally disordered and entropy-stabilized mixed metal oxides, especially consist of earth-abundant elements, using this uniformly and non-selectively adsorption method. Any progress in the above urgent problems, will make great contributions to their corresponding application fields. We hope this review can give an overview of the research progress in carbon sphere template derived hollow nanostructures, so that researchers can have a more in-depth understanding of the process and application of carbon sphere templating method, and we have given a brief description on the outlook of future development, so as to promote photocatalysis and gas sensing to practicality and benefit the development of scientific researches in these fields.

Conceptualization, Z.L. and L.Z.; Investigation, Y.W. (Yichen Wang), Y.Y., Y.W. (Yanwen Wang), C.Q., R.L., and X.C.; Writing---original draft preparation, Y.W. (Yichen Wang); Writing---review and editing, Z.L.; Supervision, Z.Y. and L.Z.; Funding acquisition, Z.Y and L.Z. All authors have read and agreed to the published version of the manuscript.

This research was funded by National Natural Science Foundation of China (51572239 and 91333203), Program for Innovative Research Team in University of Ministry of Education of China (IRT13037), the National Science and Technology Support Program (2012BAC08B08), and the Major Project of Zhejiang Natural Science Foundation of China (LD18E020002).

The authors declare no conflict of interest.

![Schematics of the possible synthesis procedure of carbon spheres. Reproduced with permission from \[[@B32-nanomaterials-10-00378]\]. Copyright WILEY, 2004.](nanomaterials-10-00378-g001){#nanomaterials-10-00378-f001}

![Proposed formation mechanism of sphere-like carbon synthesized from saccharides and biomasses. Reproduced with permission from \[[@B39-nanomaterials-10-00378]\]. Copyright American Chemical Society, 2012.](nanomaterials-10-00378-g002){#nanomaterials-10-00378-f002}

![General process for the formation of carbon sphere template derived (**a**) hollow nanoheterostructure and (**b**) controllable multilayer structure. Reproduced with permission from \[[@B47-nanomaterials-10-00378]\]. Copyright WILEY, 2016.](nanomaterials-10-00378-g003){#nanomaterials-10-00378-f003}

![(**a**) Schematic route for preparing Na-ZnO hollow nanostructures, (**b**) valence band measure of Na-ZnO with various Na doping concentrations, (**c**) corrensponding H~2~ generation for Na-ZnO/Pt hollow spheres with 0, 0.2, 0.7, 2, and 4 at % Na. Reproduced with permission from \[[@B53-nanomaterials-10-00378]\]. Copyright Royal Society of Chemistry, 2016.](nanomaterials-10-00378-g004){#nanomaterials-10-00378-f004}

![(**a**) SEM (scan electron microscope) image of broken TiO~2~ nanospheres with a macroporous channel structure by crushing THS. Reproduced with permission from \[[@B56-nanomaterials-10-00378]\]. Copyright WILEY, 2012. (**b**) Formation mechanism of the porous channels in the hollow 3D network structure. Reproduced with permission from \[[@B57-nanomaterials-10-00378]\]. Copyright Elsevier, 2012. (**c**) Schematic route for preparing C-TiO~2~\@g-C~3~N~4~. Reproduced with permission from \[[@B58-nanomaterials-10-00378]\]. Copyright Elsevier, 2017.](nanomaterials-10-00378-g005){#nanomaterials-10-00378-f005}

![(**a**) Band energy diagram of CoO*~x~*/LaTiO~2~N with1.5% Fe, and (**b**) oxygen generation rates for samples with various Fe doping concentration under visible light illumination. Reproduced with permission from \[[@B60-nanomaterials-10-00378]\]. Copyright Elsevier, 2016.](nanomaterials-10-00378-g006){#nanomaterials-10-00378-f006}

![(**a**) Schematic illustration of the band structure of anatase TiO~2~ with and without Mg doping for water splitting. (**b**) The density of states of Mg 2p in different samples. Reproduced with permission from \[[@B61-nanomaterials-10-00378]\]. Copyright Elsevier, 2017. (**c**) Mott--Schottky plot of Ta~3~N~5~ with and without Mg dopant in dark, and (**d**) normalization of the contribution of individual strategy to the photocatalytic activity. Reproduced with permission from \[[@B62-nanomaterials-10-00378]\]. Copyright Elsevier, 2019.](nanomaterials-10-00378-g007){#nanomaterials-10-00378-f007}

![Band engineering through doping and forming solid-solution. (**a**,**b**) Formation of a new VBM by doping a foreign element to create a donor level, and (**c**) forming solid solution to obtain a controllable bandgap. Reproduced with permission from \[[@B64-nanomaterials-10-00378]\]. Copyright American Chemical Society, 2004.](nanomaterials-10-00378-g008){#nanomaterials-10-00378-f008}

![(**a**) TEM image shows an extremely thin shell (about 7 nm) of (Ga~0.82~Zn~0.18~)(N~0.82~O~0.18~) hollow spheres. (**b**) The (100) peak shift between GaN (100) and ZnO (100) with different *x*. (**c**) The band structure of the (Ga~1-*x*~Zn*~x~*)(N~1-*x*~O*~x~*) nanostructures with different x. Reproduced with permission from \[[@B69-nanomaterials-10-00378]\]. Copyright WILEY, 2015.](nanomaterials-10-00378-g009){#nanomaterials-10-00378-f009}

![(**a**,**b**) TEM images of Zn*~x~*Cd~1-*x*~S hollow sphere. (**c**) UV--vis spectra of: Zn~0.5~Cd~0.5~O, Zn~0.5~Cd~0.5~S, Zn~0.7~Cd~0.3~S, Zn~0.3~Cd~0.7~S, ZnS, and CdS (**d**) XRD patterns of solid solutions of Zn*~x~*Cd~1-*x*~S after H~2~S treatment. Reproduced with permission from \[[@B73-nanomaterials-10-00378]\]. Copyright Elsevier, 2018.](nanomaterials-10-00378-g010){#nanomaterials-10-00378-f010}

![(**a**) Schematic diagram of preparation process of ZnFe~2~O~4~ nanostructures and ZnFe~2~O~4~/ZnO nanoheterostructures. (**b**) TEM images of ZnFe~2~O~4~/ZnO spheres. (**c**) H~2~ production over time by 50 mg photocatalysts of bare ZnFe~2~O~4~ and ZnFe~2~O~4~/ZnO (ZF2) sample driven by visible light (\>420 nm). (**d**) Schematic illustration of ZnFe~2~O~4~/ZnO hetrtojunction energy band position and predicted reaction mechanism under irradiation. Reproduced with permission from \[[@B80-nanomaterials-10-00378]\]. Copyright Royal Society of Chemistry, 2015.](nanomaterials-10-00378-g011){#nanomaterials-10-00378-f011}

![(**a**) Band bending diagram of Cu~2~O/crystalline Ta~2~O~5~. (**b**) Band bending diagram of Cu~2~O/amorphous Ta~2~O~5~ nanoheterojunctions. (**c**) HRTEM image of Cu~2~O/amorphous Ta~2~O~5~heterostructures. (**d**) Amount of evolved gases under full light for different samples. Reproduced with permission from \[[@B82-nanomaterials-10-00378]\]. Copyright Royal Society of Chemistry, 2017.](nanomaterials-10-00378-g012){#nanomaterials-10-00378-f012}

![(**a**) Schematic illustration of the formation path of nanoheterostructured photocatalysts. (**b**) TEM image of the TiO~2~/SnO~2~ hybrid nanostructure. (**c**) HRTEM images of the TiO~2~/SnO~2~ nanoheterojunctions. (**d**) Schematic illustration of band structure of TiO~2~/SnO~2~ heterojuction. (**e**) The PL spectra of three different hollow spheres, red line for SnO~2~, black line for TiO~2~, and blue line for TiO~2~/SnO~2~. (**f**) The photocatalytic activity measurement of different structures towards RhB under full light irradiation. Reproduced with permission from \[[@B86-nanomaterials-10-00378]\]. Copyright Royal Society of Chemistry, 2014.](nanomaterials-10-00378-g013){#nanomaterials-10-00378-f013}

![(**a**) Schematic diagram of the fabrication process of hollow hierarchical CuO/TiO~2~ structure. (**b**) SEM image of the CuO/TiO~2~ spheres. Reproduced with permission from \[[@B85-nanomaterials-10-00378]\]. Copyright 2017, RSC. (**c**) Schematic diagram of the preparation process of nest-like *γ*-Fe~2~O~3~/ZnO hollow nanostructures. (**d**) SEM images of *g*-Fe~2~O~3~/ZnO nest-like hollow nanostructures. Reproduced with permission from \[[@B88-nanomaterials-10-00378]\]. Copyright Royal Society of Chemistry, 2012.](nanomaterials-10-00378-g014){#nanomaterials-10-00378-f014}

![(**a**) The simple illustration of the synthesizing process of LaTiO~2~N nanostructures. (**b**) TEM image of LaTiO~2~N hollow nanostructures. (**c**) HRTEM image of the H~2~ treated LaTiO~2~N. (**d**,**e**) Hydrogen generation versus time on Pt/LTON and Pt/H-LTON irradiated by visible light (*λ* ≥ 420 nm) respectively. (**f**) Possible hydrogen generation principles proposed of the Pt/B-LTON, Pt/LTON and Pt/H-LTON respectively. Reproduced with permission from \[[@B95-nanomaterials-10-00378]\]. Copyright Elsevier, 2015.](nanomaterials-10-00378-g015){#nanomaterials-10-00378-f015}

![(**a**) The synthesis process of the as-prepared TiO~2~ nanostructures and black ones. (**b**) SEM image of black TiO~2~. (**c**) Time course of photocatalytic H~2~ evolution of TiO~2~ nanostructures. Reaction conditions: 20 mg photocatalysts, 1 wt % Pt loaded, under 300W Xe lamp irradiation. (**d**) EPR spectra of the as-prepared TiO~2~ hollow spheres and black ones. Reproduced with permission from \[[@B100-nanomaterials-10-00378]\]. Copyright American Chemical Society, 2017.](nanomaterials-10-00378-g016){#nanomaterials-10-00378-f016}

![(**a**) Diagrams of preparation of Au~x~\@THS\@CoO. (**b**) Production rates of CH~4~ for THS, THS\@CoO and Au~2.0~\@THS\@CoO. Reproduced with permission from \[[@B103-nanomaterials-10-00378]\]. Copyright Elsevier, 2019.](nanomaterials-10-00378-g017){#nanomaterials-10-00378-f017}

![Schematic diagram of synthesis of (**a**) core--shell, (**b**) yolk--shell Au\@TiO~2~. (**c**) UV--vis absorbance spectra for different kinds of TiO~2~ spheres. (**d**) The BET curves of yolk--shell and core--shell Au\@TiO~2~ respectively. (**e**) The possible photocatalysis principle of Au\@TiO~2~-YS. Reproduced with permission from \[[@B104-nanomaterials-10-00378]\]. Copyright Elsevier, 2019.](nanomaterials-10-00378-g018){#nanomaterials-10-00378-f018}

![(**a**) Schematic diagram of how these three proposed approaches solve the recombination problems synergistically during the photocatalytic process of Ta~3~N~5~. Red, purple, green, and yellow objects represent Ta~3~N~5~, MgO, Pt, and CoO*~x~* respectively. TEM images of (**b**) Mg-Ta~3~N~5~, (**c**) MgO/Mg-Ta~3~N~5~ and (**d**) Pt/CoO*~x~*/MgO/Mg-Ta~3~N~5~ hollow spheres. (**e**) Hydrogen generation rates of Pt/Ta~3~N~5~, Pt/Mg-Ta~3~N~5~, Pt/MgO/Ta~3~N~5~, and Pt/CoO*~x~*/MgO/Mg-Ta~3~N~5~. (**f**) Comparison between the contributions of each approach to improve the photocatalytic ability of Pt/CoO*~x~*/MgO/Mg-Ta~3~N~5~ photocatalyst irradiated under simulated sunlight. Reproduced with permission from \[[@B62-nanomaterials-10-00378]\]. Copyright Elsevier, 2019.](nanomaterials-10-00378-g019){#nanomaterials-10-00378-f019}

![(**a**) Synthetic schematic of Co~3~O~4~/Ta~2~O~5~ heterostructure hollow nanospheres, (**b**) FESEM images, (**c**) TEM images, (**d**) HRTEM images. (**e**) I--V characteristics of the Co~3~O~4~/Ta~2~O~5~ sensor. Proposed energy band diagram: (**f**) before contact, (**g**) after contact. (**h**) Response and recovery curves of the Co~3~O~4~/Ta~2~O~5~ sensor at room temperature. (**i**) Sensitivity curves between the heterostructure and pure Co~3~O~4~ sensor with 10--100 ppm. (**j**) Selective test to several reducing gases with concentration of 10--100 ppm. (**k**) Long-term stability test during two months. Reproduced with permission from \[[@B111-nanomaterials-10-00378]\]. Copyright Elsevier, 2017.](nanomaterials-10-00378-g020){#nanomaterials-10-00378-f020}

![(**a**) XRD patterns. (**b**) N~2~ adsorption and desorption isotherms and pore diameter distribution curves. (**c**) Response of all samples with different Fe doping contents from 100 to 140 °C to 1000 ppb NO~2~. The gas-sensing performance of the representative S5: (**d**) dynamic sensing curve to different NO~2~ concentrations, (**e**) dynamic response curves to 10 ppb NO~2~ at 120 °C, and (**f**) selective test to 1 ppm NO~2~ versus several 10 ppm interfering gases. Reproduced with permission from \[[@B112-nanomaterials-10-00378]\]. Copyright Elsevier, 2018.](nanomaterials-10-00378-g021){#nanomaterials-10-00378-f021}

![(**a**) Synthetic Schematic of Co~3~O~4~ NWs-HCSs. The gas-sensing performance of Co~3~O~4~ NWs-HCSs. (**b**) Sensing selectivity for several 200 ppm gases at 150 °C. (**c**) Sensing response versus operating temperature to 200 ppm acetone. (**d**,**e**) Dynamic sensing response to acetone within different concentration ranges at the operating temperature of 150 °C. Reproduced with permission from \[[@B113-nanomaterials-10-00378]\]. Copyright Elsevier, 2019.](nanomaterials-10-00378-g022){#nanomaterials-10-00378-f022}

![RH-dependent conductivity curves of (**a**) pure HCS, (**b**) HCS/PVP composite, and (**c**) annealed HCS based sensors at 40 °C. Ammonia concentration-dependent conductance and sensitivity of (**d**,**e**) pristine HCS, (**f**,**g**) HCS/PVP, and (**h**,**i**) annealed HCS based sensors at 10% RH at 40 °C. A schematic illustration of the sensing mechanism to NH~3~ of the HCSs at low RH (**j**) and high RH (**k**). Reproduced with permission from \[[@B114-nanomaterials-10-00378]\]. Copyright Royal Society of Chemistry, 2017.](nanomaterials-10-00378-g023){#nanomaterials-10-00378-f023}

nanomaterials-10-00378-t001_Table 1

###### 

Summary of carbon sphere template derived hollow nanostructure for photocatalysis.

  -------------------------------------------------------------------------------------------------------------------------------------------------------------------------------------------------------------------
  Strategy               Material                         Reaction                   Efficiency                       Reference
  ---------------------- -------------------------------- -------------------------- -------------------------------- -----------------------------------------------------------------------------------------------
  Doping                 WO~3~: Fe                        RhB degradation            *k*~RhB~ = 0.02 min^−1^          \[[@B52-nanomaterials-10-00378]\]

                         ZnO: Na                          H~2~ evolution             1380 μmol g^−1^ h^−1^\           \[[@B53-nanomaterials-10-00378]\]
                                                                                     (AQY = 13.5% @ 350 nm)           

                         TiO~2~: Nd                       *X*-3B degradation         *k~X~*~-3B~ = 0.0087 min^−1^     \[[@B54-nanomaterials-10-00378]\]

                         TiO~2~: Ce                       *X*-3B degradation         *k~X~*~-3B~ = 0.029 min^−1^      \[[@B55-nanomaterials-10-00378]\]

                         TiO~2~: C                        H~2~ evolution             35.6 μmol g^−1^ h^−1^            \[[@B56-nanomaterials-10-00378],[@B57-nanomaterials-10-00378],[@B58-nanomaterials-10-00378]\]

                         TiO~2~: Br                       RhB, MO, MB degradation    90% removal in 40 min            \[[@B59-nanomaterials-10-00378]\]

                         LaTiO~2~N: Fe                    O~2~ evolution             1.59 mmol h^−1^\                 \[[@B60-nanomaterials-10-00378]\]
                                                                                     (AQY = 55% @ 450 nm)             

                         TiO~2~: Mg                       Overall water splitting    H~2~: 850μmol g^−1^ h^−1^\       \[[@B61-nanomaterials-10-00378]\]
                                                                                     O~2~: 425μmol g^−1^ h^−1^\       
                                                                                     (AQY = 19.4% @ 350 nm)           

                         Ta~3~N~5~: Mg                    H~2~ evolution             11 μmol h^−1^                    \[[@B62-nanomaterials-10-00378]\]

  Solid-solution         (Ga~1−x~Zn~x~)(N~1−x~O~x~)       Overall water splitting    H~2~: 254.2μmol h^−1^\           \[[@B69-nanomaterials-10-00378]\]
                                                                                     O~2~: 127.1μmol h^−1^\           
                                                                                     (AQY = 14.3% @ 400 nm)           

                         Zn~x~Cd~1-x~S                    H~2~ evolution             12 mmol h^−1^ g^−1^\             \[[@B73-nanomaterials-10-00378]\]
                                                                                     (AQY = 46.6% @ 400 nm)           

  Heterostructure        ZnFe~2~O~4~/ZnO                  H~2~ evolution             2.15 mmol h^−1^ g^−1^\           \[[@B80-nanomaterials-10-00378]\]
                                                                                     (AQY = 1.61% @ 440 nm)           

                         g-C~3~N~4~/TiO~2~                H~2~ evolution             470 μmol g^−1^ h^−1^             \[[@B81-nanomaterials-10-00378]\]

                         Cu~2~O/a-Ta~2~O~5~               Overall water splitting    H~2~: 202 μmol h^−1^\            \[[@B82-nanomaterials-10-00378]\]
                                                                                     O~2~: 98 μmol h^−1^\             
                                                                                     (AQY = 3% @ 480 nm)              

                         TiO~2~/Fe~2~TiO~5~               O~2~ evolution             375 μmol g^−1^ h^−1^             \[[@B83-nanomaterials-10-00378]\]

                         ZnFe~2~O~4~/ZnSe                 H~2~ evolution             2.8 mmol g^−1^ h^−1^             \[[@B84-nanomaterials-10-00378]\]

                         TiO~2~/SnO~2~                    RhB degradation            *k*~RhB~ = 0.22 min^−1^          \[[@B86-nanomaterials-10-00378]\]

                         Fe~2~TiO~5~/TiO~2~               RhB degradation            *k*~RhB~ = 0.09 min^−1^          \[[@B87-nanomaterials-10-00378]\]

                         CuO/TiO~2~                       AO7 degradation            *k*~AO7~ = 0.057 min^−1^         \[[@B85-nanomaterials-10-00378]\]

                         γ-Fe~2~O~3~/ZnO                  RhB, MO, MB degradation    90% RhB, MB removal in 50 min\   \[[@B88-nanomaterials-10-00378]\]
                                                                                     80% MO removal in 80 min         

                         CeO~2~/TiO~2~                    RhB degradation            75% removal in 180 min           \[[@B89-nanomaterials-10-00378]\]

                         WO~3~/TiO~2~                     MB degradation             78% removal in 80 min            \[[@B90-nanomaterials-10-00378]\]

                         ZnO/CuO                          MB degradation             98% removal in 60 min            \[[@B91-nanomaterials-10-00378]\]

                         ZnO/SnO~2~                       TC degradation             81% removal in 180 min           \[[@B92-nanomaterials-10-00378]\]

                         ZnO/ZnS                          RhB degradation            99% removal in 40 min            \[[@B93-nanomaterials-10-00378]\]

  Surface modification   Surface-reconstruced LaTiO~2~N   H~2~ evolution             192 μmol h^−1^\                  \[[@B95-nanomaterials-10-00378]\]
                                                                                     (AQY = 3.4% @ 440 nm)            

                         Black TiO~2~                     H~2~ evolution             56.7 mmol h^−1^ g^−1^\           \[[@B100-nanomaterials-10-00378]\]
                                                                                     (AQY = 90.6% @ 365 nm)           

                         Pt\@TiO~2~\@MnO~x~               Benzyl alcohol oxidation   31.22 μmol in 14 h\              \[[@B102-nanomaterials-10-00378]\]
                                                                                     (AQY = 63.14% @ 254 nm)          

                         Pt/CoO~x~\@MgO~2~\@Ta~3~N~5~     H~2~ evolution             56.3 μmol h^−1^\                 \[[@B62-nanomaterials-10-00378]\]
                                                                                     (AQY = 0.31% @ 400 nm)           

                         Au~2.0~\@TiO~2~\@CoO             CO~2~ reduction to CH~4~   13.3μmolh^−1^g^−1^               \[[@B103-nanomaterials-10-00378]\]

                         Yolk--shell Au\@TiO~2~           Toluene degradation        57% removal in 180 min           \[[@B104-nanomaterials-10-00378]\]
  -------------------------------------------------------------------------------------------------------------------------------------------------------------------------------------------------------------------

nanomaterials-10-00378-t002_Table 2

###### 

Summary of carbon sphere template derived hollow nanostructure for gas sensing.

  Strategy               Material              Gas       Response                Reference
  ---------------------- --------------------- --------- ----------------------- ------------------------------------
  Doping                 WO~3~: C              acetone   5.1 @ 0.9 ppm, 300 °C   \[[@B109-nanomaterials-10-00378]\]
                         WO~3~: Fe             NO~2~     1.3 @ 10 ppb, 120 °C    \[[@B112-nanomaterials-10-00378]\]
  Heterostructure        Pd\@In~2~O~3~         ethanol   159 @ 5 ppm, 350 °C     \[[@B108-nanomaterials-10-00378]\]
                         Co~3~O~4~/Ta~2~O~5~   ethanol   1.8 @ 100 ppm, 25 °C    \[[@B111-nanomaterials-10-00378]\]
                         Co~3~O~4~\@C          acetone   23 @ 200 ppm, 150 °C    \[[@B113-nanomaterials-10-00378]\]
  Surface modification   Annealed C            ammonia   66 @ 74 ppm, 40 °C      \[[@B114-nanomaterials-10-00378]\]
