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Title: Recent Advances of MOF-Derived Nanoporous Carbon Materials
Authors: Freddy Marpaung; Konstantin Konstantinov; Yusuke Yamauchi; Md.Shahriar A. Hossain; Jongbeom Na; Jeonghun Kim
This is the author manuscript accepted for publication and has undergone full peerreview but has not been through the copyediting, typesetting, pagination and proofrea-ding process, which may lead to differences between this version and the Version ofRecord.
To be cited as: Chem. Asian J. 10.1002/asia.201900026
Link to VoR: https://doi.org/10.1002/asia.201900026
This article is protected by copyright. All rights reserved
Recent Advances of MOF-Derived Nanoporous Carbon Materials
Freddy Marpaung,+1,2
Konstantin Konstantinov,1 Yusuke Yamauchi,*
2,3,4,5, Md. Shahriar A. Hossain
2,6
Jongbeom Na,*2,3
and Jeonghun Kim*
2
1 Australian Institute for Innovative Materials (AIIM), University of Wollongong, North Wollongong,
NSW 2500, Australia
2 Australian Institute for Bioengineering and Nanotechnology (AIBN), The University of Queensland,
Brisbane, QLD 4072, Australia
3 International Center for Materials Nanoarchitectonics (WPI-MANA), National Institute for Materials
Science (NIMS), 1-1 Namiki, Tsukuba, Ibaraki 305-0044, Japan
4 School of Chemical Engineering, The University of Queensland, Brisbane, QLD 4072, Australia
5 Department of Plant & Environmental New Resources, Kyung Hee University, 1732 Deogyeong-
daero, Giheunggu, Yongin-si, Gyeonggi-do 446-701, South Korea
6 School of Mechanical & Mining Engineering, The University of Queensland, Brisbane, QLD 4072,
Australia
+ These authors equally contributed to this work.
E-mails: [email protected]; [email protected]; [email protected]
Abstract
Metal-organic frameworks (MOFs)-derived nanoporous carbon materials have received significant interest
due to their advantages of controllable porosity, good thermal/chemical stability, high electrical conductivity,
catalytic activity, easy modification with other elements and materials, etc. Thus, MOF-derived carbons
have been used in numerous applications such as environment, energy storage systems (i.e., batteries,
supercapacitors), catalysts, etc. Until now, many strategies have been developed in order to enhance the
properties and performances of MOF-derived carbons. In this review, we introduce and summarize recent
important approaches for advanced MOF-derived carbons focusing on precursor control, heteroatom doping,
shape/orientation control, hybridization with other functional materials.
Keywords: nanoporous carbon; metal-organic frameworks; functional carbon; chemical synthesis
Introduction
Carbon is one of the most important elements and can be existed with different forms such as graphite,
diamond, fullerene, and amorphous carbon. To improve their performances, nanoporous structure have been
introduced into carbon because nanopores can give a large surface area. Importantly, nanoporous carbon
materials (NPCs) have showed unique properties such as good electrical conductivity, catalytic activity, and
good thermal/chemical stability. These outstanding properties make them attractive to be used in various
applications such as purification of environments, energy storage systems (i.e., batteries, supercapacitor),
and catalysts. Until now various carbon materials with different pore sizes ranging from micropores to
macropores have been extensively studied. There are lots of carbon materials produced from series of
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carbonization and activation process which possess controllable pore structures, which include activated
carbon, templated porous carbons, etc. Templated carbon materials have been prepared by various
approaches such as direct carbonization from carbon precursors, soft- and hard-templating methods. In order
to enhance the electrochemical performance of the electrode materials, heteroatoms, such as nitrogen (N),
sulfur (S), and boron (B), have been doped into porous carbons.
However, the large-scale synthesis is difficult in terms of cost-effectiveness because these methods
require numerous synthesis steps. To overcome the shortcomings, researchers have tried to solve those
issues by using metal-organic frameworks (MOFs) as sacrificial templates/precursors.[1-2]
MOFs have gained
a considerable attention in recent years because of their abundant diversity in structure and composition. In
addition, the porosity of MOFs can be tuned by organic linkers. More interestingly, their structures and
functions can be tailored for on demand applications through the transition metal ions and organic linkers.[3-
5]
In this review article, we summarize recent works for the synthesis, structural characteristics and
functionalization of MOF-derived NPCs. Much attention will be given on the new discoveries of MOF-
derived NPCs which are derived from MOFs precursors with different organic or inorganic functional
moieties such as N, Co, Sn, Ni, P and hybrid NPCs incorporated with metal oxides, metal nanoparticles. We
also elaborate how these added functionalities may affect the final performance of NPCs in electrochemical
applications.
History of MOFs-derived NPCs
Xu et al. reported the fabrication of MOF-derived NPC using MOF template with organic additives.[6]
The
furfurals alcohol (FA) having a molecular dimension of 8.4×6.4×4.3 Å3 has been used as a carbon source.
[7]
FA was infiltrated into the micropores of the MOF-5 by CVD process and subsequently polymerized. Then,
the decomposition of MOFs and the formation of NPC frameworks occurred simultaneously during
carbonization in an inert atmosphere. The resulted NPC how a high surface area (2,872 m2
g-1
) after
carbonization at 1000 ºC. At low carbonization temperatures, such as 530 ºC (the decomposition point) or
800 ºC, the surface areas were 217 or 417 m
2 g
-1, respectively. FA has been successfully infiltrated into
MOF and MOF acted as both sacrificial template and secondary carbon source. Later, same group reported
the NPCs with surface area in range of 1,141 to 3,040 m2
g-1
through the wet impregnation method using FA
under a low carbonization temperature.[8]
After polymerization of FA and pyrolysis process, hierarchically
porous carbon materials were successfully obtained. From these approaches, it has been found that the pore
size was depended on the method of penetration of carbon source into the cavities of MOF-5 and the
carbonization condition. These methods opened the utilization of many alternative carbon sources such as
glycerol, carbon tetrachloride, ethylenediamine, and phenolic resin for preparation on MOF-derived NPCs.[9-
10]
Owing to large amount of carbon source from organic linker in MOFs, direct pyrolysis of MOFs
without any additional carbon sources can also lead to synthesize the NPCs.[11-12]
Cendrowski et al.
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demonstrated of NPCs through direct carbonization of MOF-5 at different temperature under argon
atmosphere.[13]
After carbonization at temperature between 700 and 900 ºC, they showed a tendency for
agglomeration which significantly reduced the surface areas from 2,524 m2
g-1
to 1,153 m2
g-1
and 1,892 m2
g-1
, respectively. From these cases, a highly nanoporous carbons can be obtained through the carbonization
at a lower temperature.
NPCs derived from MOFs possess many advantages such as extremely high surface area, uniform
pore sizes, large pore volume, good thermal and chemical stability. We can expect a wide range of
applications including water purification for drinking water, energy harvesting, energy and gas storage,
absorbents, and catalysts. Recently, many efforts have been made to upgrade the performance of the MOF-
derived NPCs.
Various types of MOFs as precursors
Up till now, considerable efforts have been conducted to synthesis NPCs with uniform particle sizes and
shapes due to their potential applications in many aspects. So far, a wide variety of MOFs, such as MOF-
5,[14]
ZIF-8,[15]
ZIF-67,[16]
MOF-199,[17]
UiO-66,[18]
MIL-53,[19]
and Cu3(BTC2)[20]
have been considered as
promising carbon precursors for synthesizing NPCs. A wise selection of MOFs as precursors (inorganic
connectors and organic ligands) plays an important role for determination of the resulting structural
properties of NPCs. Following the above report, Chang et al. controlled the particle sizes of MOF-525 from
100 nm to 750 nm.[21]
After carbonization, they carefully investigated the effect of variation of the particle
sizes on the electrochemical performance have been investigated.
Kim et al. successfully investigated the direct pyrolysis of a series of well-known nonporous Zn-
containing MOFs and found that they can lead to the formation of NPCs with high nanoporosity.[22]
The
same group also proposed a linear relationship between the Zn:C atomic ratio from the starting MOF and the
corresponding SA of the obtained NPCs. This result showed an easy control of surface area by Zn/C ratio of
the precursors. Interestingly, the field of MOF structures has been extended towards the metal-organic gels
(MOGs).[23-24]
The coordination framework of the synthesized materials were made by hydrogen bonding
and Van der Waals force.[25]
Zou et al. reported a facile way to prepare NPCs from Al-based MOGs (Al-
MOGs).[23]
The resulted NPCs exhibited an impressive porous property of exceptionally high surface area
and large pore volume of 3,770 m2
g-1
and 2.62 cm3 g
-1, respectively because of a hierarchical porous
architecture. These NPCs showed a considerable hydrogen uptake and superior electrochemical.
Zhao et al. develop carbonized nanoparticles, which are derived from monodisperse nanoscale metal
organic frameworks (MIL-88B-NH3), as the high-performance ORR catalysts.[26]
The obtained onset
potential and the half-wave potential for the ORR represent the best ORR activity of all the non-noble metal
catalysts reported so far. Thus, we should explore new MOFs as sacrificial templates for realizing the best
catalytic performance.
Morphological controls
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Peng and co-workers synthesized porous carbon polyhedral (PCP) materials that were derived from Zn-
PBAI MOF (Figure 1a).[27]
The Zn-PBAI was constructed through combining T-shaped ligand, 5(4-
pyridine-4-yl-benzoylamino) isophthalic acid ligands with pyridine and isophthalate. The formation of
polyhedron shape was initiated by the interaction between six Zn atoms and six PBAI ligands to generate an
octahedral supramolecular building block. A 3-D porous metal-organic polyhedral framework was created
through connecting each of octahedral cage. They carbonized the Zn-PBAI at different temperature (800,
900 and 1000 ºC) under a nitrogen atmosphere, the surface areas increased significantly from 1,037 m
2 g
-1
(PCP-800), 1,160 (PCP-900), and 1,254 m2
g-1
(PCP-1000), respectively. Furthermore, the porous carbons
showed high performance in electrochemical analysis. Especially, the PCP-1000 showed the high capacity
which was attributed to the high surface area which provide abundant of active venues for the storage and
transmission of Li ions. Besides, both of nitrogen and pyridinic can improve the functionalization of the PCP,
as well as strengthen the bonding of lithium species and receive more charge from Li ions.
The hollow carbon nanobubbles were successfully synthesized through chemical etching techniques
by Zhang et al. (Figure 2a).[28]
The hollow structures on the ZIF-8 were prepared by chemical etching using
tannic acid, in which the tannic acid was used either as a protecting agent or an etching agent. In order to
further expand the mesopores, they carbonized it at 600 oC under N2 atmosphere followed by removal of
remaining Zn with HCl solution. As a result, a wide range pore size distribution was shown for the hollow
carbon nanobubbles, including micropores (< 2 nm) and mesopores in the range of 6 to 40 nm. However, the
surface area of hollow carbon nanobubbles was only 700 m2
g-1
, which was lower than that of the non-
hollow carbon nanoparticles (900 m2
g-1
).
Recently, ordered-porous metal-free carbon (o-PMFC) with uniform rod-like morphology was
successfully synthesized (Figure 1d) by using Zn-MOF nanorods.[29]
Interestingly, the formation of rod-
shaped morphology (Figure 1e and f) occurs without surfactants and modulators. After the sample was
carbonized in N2 atmosphere, the o-PMFC was successfully obtained. This material demonstrates good
water dispersibility and strong interaction with glycans. When used to capture N-glycans, the o-PMFC
showed a higher absorption capacity compared with activated carbon. Recently, Xu et al. reported a self-
templated, catalyst-free strategy for the synthesis of one-dimensional carbon nanorods by morphology-
preserved thermal transformation of rod-shaped MOFs. The as-synthesized non-hollow (solid) carbon
nanorods can be transformed into graphene nanoribbons through sonochemical treatment followed by
chemical activation. This approach without any complicated steps is readily scalable and could be used to
produce carbon nanorods and graphene nanoribbons on industrial levels.[30]
Other group has successfully synthesized nano-diatom porous carbon by introduced of guest species,
as shown in Figure 3d.[31]
They obtained porous carbon with different shapes of nanoparticles such as
polyhedral, fiber and web-like (Figure 3b-e) after pyrolysis at 800 ºC under argon atmosphere. When applied
to Li-B batteries, the nano-diatom electrode can deliver a capacity of up to 830 mA h g-1
in the primary
discharge/charge after 10 cycles at a current density of 0.2 A g-1
and over 600 mA h g-1
after 10 cycles at a
current density of 1 A g-1
. Interestingly, this electrode material showed capacity retention of over 75% after
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500 cycles. When compared with current commercial graphite electrodes, the nano-diatom electrode showed
a better stability and performance. Such excellent performance was attributed to their unique structures
which were important for improving electrolyte access to the active sites.
For practical applications of supercapacitors, direct preparation of electrode on the conductive
substrates is crucial in order to diminish the resistance between the electrode material and the current
collector. Therefore, recently our group developed a new method for fabricating ZIF-8 and ZIF-67
nanowires through a simple and facile chemical vapor deposition on a conductive carbon cloth (Figure 4).[32]
This approach opens up a new way for solvent-free synthetic route of MOFs. The Co3O4-loaded NPC
nanowire arrays were fabricated by further thermal treatment. Co3O4 is known as a faradic metal oxide with
a high theoretical capacitance. Due to the presence of Co catalyst, ZIF-67 was successfully converted to
highly conductive sp2 type carbon. The obtained hybrid electrodes exhibited a high areal capacitance with
stable cycling. A simple synthesis of MOFs via the chemical vapor method offers a promising new platform
to design conductive, ultra-high surface area carbon electrodes.
Ma et al. also reported hybrid porous nanowire arrays composed of strongly interacting Co3O4 and
carbon were prepared by a facile carbonization of the MOF grown on Cu foil. The resulting material,
possessing a high surface area and a large carbon content, can be directly used as the working electrode for
oxygen evolution reaction without employing extra substrates or binders. The resulting hybrid Co3O4-carbon
porous nanowire arrays can also efficiently catalyze oxygen reduction reaction, featuring a desirable four-
electron pathway for reversible oxygen evolution and reduction, which is potentially useful for rechargeable
metal–air batteries, regenerative fuel cells, and other important clean energy devices.[33]
Meng et al. develop a general method for the oriented synthesis of precise carbon-confined
nanostructures by low-pressure vapor superassembly of a thin MOF shell and subsequent controlled
pyrolysis.[34]
The selected nanostructured metal oxide precursors not only act as metal ion sources but also
orient the superassembly of gaseous organic ligands through the coordination reactions under the low-
pressure condition, resulting in the formation of a tunable MOF shell on their surfaces. This synthetic
approach and proposed mechanism open new avenues for the development of functional nanostructured
materials in many frontier fields.
Introduction of heteroatoms into MOF-derived carbons
Nowadays, introduction of heteroatoms such as sulphur, boron, nitrogen into the carbon structure can
enhance the physical, chemical and electrical properties of NPCs.[35-37]
For example, nitrogen-doping can
enhance electrochemical performance, which has promising potentials as catalysts, H2 storage, CO2
adsorbents, and electrode materials. Wang et al. reported the functionalization of NPCs via nitrogen doping
that could enhance the catalytic performance. The porous carbon was prepared by direct carbonization of
ZIF-8 precursors at different temperature (700, 800, and 900 ºC) in N2 followed with removal of zinc oxide
nanoparticles using acid treatment (Figure 5).[38]
The resulting materials were applied as a electrocatalyst in
the electrochemical reduction of carbon dioxide. Interestingly, the Faradaic efficiencies to carbon monoxide
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(∼78%) reached as high as about 78%. The carbonization temperature can control the amount and the
accessibility of N species in the NPCs, in which pyridinic-N and quaternary-N species play key roles in the
selective formation of carbon monoxide.
Wu and co-workers synthesized dual-heteroatom doped-hollow carbon via synergistic etching and
surface functionalization by using tannic acid.[39]
ZIF-8 were served as both a precursor and a nitrogen-
source, while 1,4-benzene diboronic acid (DBBA) was used as a boron-source. After carbonization with the
assistance of tannic acid, N/B co-doped hollow carbon materials were obtained. The excellent ORR
performances can be assigned to the large surface area and the existence of co-doping B and N which can act
as active sites to facilitate oxygen absorption and reduction.
Very recently, Ma et al. investigated the tri-doped (N, P, and S) hollow carbon shells (NPSC).[40]
The
NPSC materials were prepared by mixing ZIF-67 with poly(cyclotriphosphazeneeco-4,40-sulfonyldiphenol)
followed with pyrolysis at different temperature in N2 and acid etching (Figure 6a). The porous hollow shells
were successfully doped with N, S, and P, as shown in Figure 6b-f. Such heteroatom-doped carbon materials
are attractive catalysts for peroxymonosulfate (PMS) activation and environment remediation. The
synergistic effects of N, P, and S doping greatly break the electroneutrality of pristine carbon structures,
promote the O-O breakage of PMS, and facilitate the generation of radicals.
Oxygen co-doped NPC is useful for enhancement of absorption capacity for methylene blue (MB).
This NPCs were prepared by direct carbonization process of MOFs under an inert gas streamed with water
steam.[35]
The water steam acts as the oxidizing and activating agent. The steam-water treatment increased
the concentration of O in the sample. When evaluated the absorption capacity for methylene blue (MB)
showed that sample without streamed of water steam has a higher absorption capacity.
Functionalization with nanoparticles (metals, metal oxides, metal sulfides, etc.)
It is interesting to extend the synthetic method to further enhancement the properties of NPCs through the
deposition of functional metal, metal oxide, metal sulphide nanoparticles into NPCs. Magnetic Co/NPC
composites were prepared by direct one-step carbonization of ZIF-67, a well-known Co-containing MOF.[41]
Unlike the previously mentioned methods, this approach can maintain a rich content of highly crystalline
magnetic Co nanoparticles that are uniformly distributed over the entire NPCs. Therefore, the obtained
Co/NPC composite shows a strong magnetic response. Cheng et al. reported a successful deposition of Cu
nanoparticles on MOF-5-C which was fabricated by direct carbonization of MOF-5 without any additional
carbon sources.[42]
The surface area of MOF-5-C (2,524 m2
g-1
) was higher than that of Cu@MOF-5-C
(2,039 m2
g-1
). In the catalytic activity for the A3-coupling reactions, the Cu@MOF-5-C had a higher
catalytic activity, even with smaller surface area. This occurs due to synergetic interaction between Cu
nanoparticles and the matrix of porous carbon. Guo et al. synthesized Sn@NPC in two steps; (1)
carbonization of ZIF-67 at temperature of 800 ºC under argon atmosphere followed with removal Co
nanoparticles using hydrochloric acid, and (2) chemical reduction of Sn species in the NPCs. The Sn
nanoparticles were uniformly dispersed into the carbon matrix.[43]
The surface area of the NPC before Sn
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deposition was 547 m2
g-1
, the Sn deposition largely decreased to 134 m2
g-1
. When this material was used as
anode materials for Lithium-ion battery, it showed good electrochemical properties which achieved high
initial discharge and charge capacities (1,440 mA h g-1
and 818 mA h g-1
at a current density of 200 mA g-1
).
In addition, this material had 51% capacity retention (741 mA h g-1
) even after 200 cycles at a current
density 200 mA g-1
. Such high Li storage capacity and excellent rate of capability can be associated to the
unique carbon frameworks, which provide abundant active sites and to buffer the strain due to volume
change during charging and discharging process upon cycling.
Jiao et al. has successfully synthesized magnetic NPCs (Fe3O4/NPC) which was derived from MOF-5
and Fe salt that were used as a carbon and a magnetic precursor, respectively (Figure 7a).[44]
The synthesized
Fe3O4/NPC was obtained through in situ chemical co-precipitation of Fe2+
and Fe3+
on the NPCs. Then it is
followed by carbonization at 900 ºC in nitrogen atmosphere. The TEM and SEM images (Figure 7b-e)
clearly show that nano-sized Fe3O4 particles were dispersed homogeneously on the matrix of NPC. The
adsorption performance also showed high adsorption capacity (292.4 mg g-1
at 298 K) and rapid adsorption
rate for organic dye methylene blue (MB). This material can be used as an absorbent for various organic
dyes. Haldorai et al. synthesized NPC-Co3O4 composite from ZIF-67 at temperature 900 ºC under nitrogen
atmosphere with removal of Co nanoparticles with 10% HF solution (Figure 8a).[45]
At evaluation of
electrodes for pseudocapacitors, the synthesized materials that is NPC-Co3O4 composite showed a high
specific capacitance of 885 F g-1
at 2.5A g-1
. An excellent stability was gained with only 6.0% capacitance
loss after 10,000 cycles. Besides that, the NPC-Co3O4 could be used as an electrode for the detection of
glucose. The improvement is from the synergistic effects between components in the nanostructured NPC-
Co3O4 composite, as well as a high surface area and higher ionic conductivity than that of the NPC.
Chen et al. also prepared porous carbon composites (Ni1Co4S@C) using Ni substituted ZIF-67 as
precursor via a one-step simultaneous carbonization and sulfurization process.[46]
The metal sulphide
nanoparticles were homogeneously embedded into the matrix of porous carbon that remarkably strengthens
the interaction between metal sulphides and carbon matrix. The large surface area is provide enough sites for
diffusion of ions through the highly porous substructures, which are crucial for the electrochemical activity
the electrodes. These findings pave a way to develop effective and promising alternative electrocatalysts
towards OER, ORR and HER in the next generation of energy storage and conversion technologies. Another
group also reported a porous Cu@graphitic octahedron carbon cages from a Cu-based MOF. The resulting
material exhibited good enrichment ability for four fluoroquinolones (FQs) due to their superior chemical
affinities to the target analytes.[20]
Unique catalytic effect of Co nanoparticles to grow carbon nanotubes
Meng et al. synthesized ZIF-67, followed with thermal treatment at a low temperature of 435 ºC under argon
(Figure 9a).[47]
Interestingly, the reducing gasses such as H2 and NH3 were released during pyrolysis reaction,
which it could alter metal ions into metal nanocatalysts that beneficial to catalyze the organic ligands and
generate a highly oriented CNTs. The growth direction of CNTs is from inside to outside, which create a
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hollow interior voids after the carbonization process. The obtained hollow dodecahedra (N-CNTs-650)
showed increasing catalytic activities toward ORR (0.85 V), compared to Pt/C (0.83 V) in 0.1 mol L-1
KOH
solution saturated by oxygen. In addition to the outstanding ORR mentioned above, the composite displayed
a discharge capacity of 1,030 mA h g-1
after 250 cycles at a current rate of 0.1 A g-1
. The hollow interior
space and multilevel pores also allow fast diffusion of charged species onto the surface of the active sites.
Another type of NPCs was prepared from a bimetallic ZIF that is composed of Co2+
and Zn2+
with 2-
MIM as an organic linker (Figure 10a).[48]
After carbonization, the samples were washed extensively with
acid HF solution to remove the residual Zn and Co. Interestingly, a large portion of multiwalled CNTs
(MWCNTs) on the matrix of NPCs was observed. When evaluated as electrode for capacitor, the NPC
showed the potential window up to 0.8V and specific capacitance at about 10 Fg-1
at all current densities,
even at high current density (10 A g-1
). Such outstanding electrochemical behaviour can be ascribed to the
presence of CNTs, which provide abundant active sites for improving the electrical conductivity and
enhancing ion diffusivity. Kim and co-workers successfully synthesized another hybrid NPC derived from
ZIF-8 (Zn2+
) and ZIF-67 (Co2+
) (Figure 11a), and subsequently carbonized the obtained material at
temperature of 800 ºC under argon condition.[49]
The presence of hairy-like CNT on the surface of NPC
derived from Co/Zn-ZIF, as shown in Figure 11c and d. The electrochemical performance of the materials
showed the high capacitance values of 286 F g-1
at 2.5 A g-1
and 103.7 F g-1
at 10 A g-1
by investigation in
the 3 electrode configuration using 0.5 M H2SO4 electrolyte.
The highly uniformed hybrid carbon material has been prepared by in-situ growth carbon nanotubes
(CNTs) from MOFs, with the cobalt species as the catalyst for CNTs growth and dicyandiamide (DICY) as a
sacrificial agent for the formation of graphitic carbon.[50]
The polygonal structures and CNTs could be
observed on the edge of polygon carbon from the SEM images (Figure 12b-d). The cobalt nanoparticles and
heteroatom nitrogen can help in immobilizing sulfur species, resulting in the formation of a hybrid
composite (CNT@Co-N-C/S). This electrode material is capable of attaining up to 970 mA h g-1
of energy
density at 0.2C. Furthermore, it showed a good stability with nearly 79.8% of the capacity retention after
500 cycles. This excellent performance is supported by the formation of Co nanoparticles which are
distributed on the carbon matrix (Figure 12e). In addition, the CNT@Co-N-C/S showed high electrical
conductivity because of CNT on the carbon-sulphur composites that can not only shorten the penetration of
ions into the porous structure but also facilitate access of electrolyte. Similar phenomenon was reported by
Huang et al. New nanocomposites consisting of nanostructured Co3O4 and multiwalled carbon nanotubes
(MWCNTs) is highly desirable for the improvement of electrochemical performance of lithium-ion
batteries.[51]
Hybridization of MOF-derived NPCs with carbon nanotubes, graphene nanosheets, and related
nanomaterials
Hybridization has been known as an effective way to upgrade the functionalities and stabilities of NPCs.
Tan et al. reported the hybridization of ZIF-8 with CNTs, as shown in Figure 13a.[52]
The ZIF-8 was used as
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precursors and CNT as a skeleton for assembly of ZIF-8 nanocrystals. The obtained hybrid materials after
carbonization at 1,000 ºC in a N2 atmosphere were clearly confirmed by the SEM and TEM images (Figure
13b and c). The relatively high specific capacitance (up to 75.1 F g-1
at 1 A g-1
in 1M H2SO4 solution) was
realized, which was attributed to the strong interaction between carbons and CNTs. Another group also
developed the following similar approach.[53]
The ZIF-CNT hybrid material was carbonized at 1000 ºC
under Ar atmosphere. The additional injection of NH3 (10 vol%) increased the N content in the obtained
material. The optimized sample showed a half potential (E1/2) of 0.899 V in 0.1 M KOH, which was higher
than that of Pt/C (E1/2 = 0.881 V). Furthermore, this catalyst showed a higher ORR onset potential of 1.05 V,
compared to Pt/C (1.02 V). The specific activity at 0.80 V was over 700 mA cm-2
, which was also much
higher than that of Pt/C catalyst (114.4 mA cm-2
). The superior catalytic performance was mainly associated
to the synergistic effects between NPC and CNT along with abundant N content. Bao et al. reported a
hierarchical architecture of multi-walled carbon nanotubes @ mesoporous carbon (MWCNT@Meso-C)
using unique multi-walled carbon nanotubes @ metal-organic framework (MWCNT@MOF-5) as both
template and precursor. Active sulfur is encapsulated into the MWCNT@Meso-C matrix for high
performance lithium sulfur battery. The resulting MWCNT@Meso-C is a promising host material for the
sulfur cathode in the lithium sulfur battery applications.[54]
Another work was performed by Park et al., in which NPCs were functionalized with crumpled
graphene balls (CGBs) (Figure 14a).[55]
The CGBs act as a conductive matrix for the formation of
polyhedral MOF which utilized vander Waals forces between the CGBs and organic precursor. The
polyhedral MOF was carbonized at 700 ºC in an argon atmosphere, followed with spray pyrolysis of CGBs
and diffusion of Se into the micropores of carbon matrix. The discharge capacity of the NPC/CGB-Se
electrode in lithium-selenium battery was up to 998 mA h g-1
at current density of 0.5 C in a non-aqueous
electrolyte. In addition, the NPC/CGB-Se had a remarkable cycle stability with discharge capacity 462 mA h
g-1
over 1000 cycles. Such excellent of electrochemical properties can be associated to the unique pore
structure of the composite, which can not only increase Se-ion diffusion but also enhance electrolyte
penetration. Ge and co-workers reported a synthesis of MOF-derived core/shell structured CoP@C
polyhedrons anchored on 3D reduced grapheme oxide (RGO) on nickel foam (NF) as binder-free anode for
high performance sodium-ion battery (Figure 15).[56]
The ZIF-67-GO-NF was first prepared at room
temperature and then carbonized and phosphatized at 400 oC. Further carbonization of ZIF-67-RGO-NF was
performed at temperature 350 ºC in argon atmosphere to obtained ZIF-67-derived core/shell Co@C
polyhedral structure. After that, an in-situ low-temperature phosphidation process was carried out to obtain
CoP@C polyhedrons. This hybrid material showed a higher initial discharge/charge capacity
(2,455.6/1,163.5 mA h g−1
) compared to CoP@C (1,908.5/746.2 mA h g−1
) in sodium-ion battery test. In
addition, the electrode was able to retain 47.3% of its original capacity after 100 charge-discharge cycles.
Such high initial charge/discharge capacity and stability can be ascribed to the unique core/shell structured
CoP@C and RGO networks, which can accommodate diffusion of species through the highly porous
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substructures and buffer of volume changes during charge and discharge process, which are essential for the
electrochemical activity of electrodes.
Jin and co-workers reported that natural halloysite nanotubes (HNTs) were hybridized with MOFs to
prepare novel composites.[57]
Pre-treatment using sulfuric acid and nitric acid mixed solution was key obtain
halloysite with carboxylic group. Then, the halloysite was mixed with triethylamine and DMF to produce
MOF/ halloysite composite, followed by calcination in N2. The resulting carbon material showed good
hydrogen absorption of 0.23 wt% at 2.65 MPa. Further decoration with transition metals such as Al, Pd and
Ni enhanced the hydrogen absorption performance. The Pd-loaded carbon material had higher hydrogen
absorption of 0.32 wt% at 25 ºC and 2.65 MPa.
Conclusion and Perspectives
In our review, we demonstrate that the NPCs synthesized from MOFs through appropriate functionalization
methods can be applied to numerous applications. By precisely tuning the pore structures, shapes,
framework compositions, many benefits can be realized such as improving magnetic property, catalytic
activity, absorption capacity, and capacitance. By controlling the shapes of the starting MOF crystals, we
can prepare many kinds of MOF-derived NPCs such as hexagonal, cubes, hollow spheres, flakes, tubes, and
foams. Heteroatom doping and encapsulation of nanoparticles dispersed on the NPC matrixes are very
effective to optimize the physical and chemical properties. However, there are still many obstacles that need
to be overcome in order to synthesis highly ordered NPCs derived from MOFs. A better approach to finely
control the pore sizes of carbon nanoparticles is required. Future works should figure out how to determine
the shapes and sizes of carbon nanopores and find the best way to transfer guest species onto the nanopores
carbon surface. We are expecting to discover new structures of NPCs derived from MOFs, and we believe
that the resulting new NPCs will be extended into other undiscovered research sectors to diverse
applications with more investigation in the further.
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Figure 1. (a) Schematic synthesis of porous carbon polyhedral (PCP), (b, c) SEM images of PCP.
[27] (d)
Schematic preparation procedure of porous metal free carbon (PMFC), (e, f) SEM images of PMFC.[29]
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Figure 2. (a) Schematic illustration of the synthesis of NPC nanobubbles (b) The SAED pattern of NPC
nanobubbles, (c) The particle size distribution of NPC nanobubbles.[28]
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Figure 3. (a) Preparation precedures for fabrication of nano-diatom derived from guest impregnation of
polyhedral MOF. The SEM images of nano-diatom for (b, c) web-like surface and (d, e) fiber-like
structure.[31]
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Figure 4. Scheme showing the synthetic process to generate (a) ZnO@ZIF-8-x-y and
Co(CO3)0.5(OH)·0.11H2O@ZIF-67-x-y using 2-Melm vapor where x and y are the synthesis temperature
and synthesis time, respectively. (b) Advantages of Co3O4/NC hybrid materials. (c, g) SEM images of (c) the
original ZnO-arrays and (g) Co(CO3)0.5(OH)·0.11H2O-arrays grown on conductive carbon cloth. (d) Low
magnification and (e) high magnification SEM images, and (f) TEM image of the ZnO@ZIF-8 sample
grown at 100 °C for 15 h (i.e., ZnO@ZIF-8-100-15). (h) Low magnification and (i) high magnification SEM
images, and (j) TEM image of the Co(CO3)0.5(OH)·0.11@ZIF-67 sample grown at 90 °C for 15 h (i.e.,
Co(CO3)0.5(OH)·0.11H2O@ZIF-67-90-15).[32]
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Figure 5. (a) Preparation procedures for synthesis of N-doped NPC. i) Room temperature synthesis of ZIP-8
crystals. ii) Pyrolysis of the ZIF-8 crystals in N2. iii) Acid leaching to generate the N-doped NPC catalyst.
The TEM images of (b) ZIF-8 and (c) N-doped NPC.[38]
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Figure 6. (a) Preparation of NPSC at different temperature (600, 700, 800 °C) from ZIP-67 and PZS. The
SEM images of (b) ZIF-67, (c) NPSC-600, (d) NPSC-700, and (e) NPSC-800; TEM images of (f) ZIF-67,
(g) NPSC-600, (h) NPSC-700, and (i) NPSC-800.[40]
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Figure 7. (a) Preparation procedures for synthesis of Fe3O4/NPC. The SEM images of (b) NPC, and (c)
Fe3O4/NPC. The TEM images of (d) NPC and (e) Fe3O4/NPC.[44]
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Figure 8. (a) Schematic images of the fabrication of NPC-Co3O4 composite for glucose sensor and
supercapacitor applications. (b) The SEM image of the as-synthesized ZIF-67 and (c) TEM image of NPC-
CO3O4.[45]
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Figure 9. (a) Preparation procedures for the synthesis process of N-CNTs from ZIF-67. The corresponding
SEM images of (b) fresh ZIF-67 and (c) samples prepared after low-temperature pyrolysis at 435 °C in argon
for 0.5 h and (d) 8 h, respectively. (e, f) SEM, (g, h) TEM and (i) HRTEM images of N-CNT-assembled
hollow dodecahedra.[47]
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Figure 10. (a) Schematic procedure for synthesis of bimetallic Co/Zn ZIF. The SEM images of (b)
bimetallic ZIF and (c) carbonized hybrid ZIF. The TEM images of (d) residual Co particles and (e) graphitic
carbon nanotudes (CNTs) on the surface of the as-prepared nanoporous carbon.[48]
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Figure 11. (a) Schematic procedure for synthesis of hybrid Co/Zn (2:1)-ZIF from metal precursors and 2-
methylimidazole ligand, and carbonization to form amorphous and graphitic nanoporous carbon. The SEM
images of (b) hybrid Co/Zn (2:1)-ZIF, (c) carbonized nanoporous carbon (NPC), and (d) CNT on the surface
of NPC. (e) High resolution (HR)-TEM image of CNT on the surface of NPC. (f, g) TEM images, (h) high-
angle annular dark field – scanning TEM (HAADF-STEM) image, and (i) EDS mapping of hybrid Co/Zn-
ZIF.[49]
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Figure 12. (a) Illustration of the synthesis of CNT@Co-N-C, SEM images of (b) ZIF-67, (c) Co-N-C and
(d) CNT@Co-N-C carbonization at 700 oC with 30% DICY, (e) TEM images of CNT@ Co-N-C.
[50]
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Figure 13. (a) Schematic illustration of the synthesis of N-doped NPC from ZIF-8/CNT, NPC composite
images (b) SEM, (c) TEM.[52]
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Figure 14. (a) The schematic diagram of NPC/CGB-Se Composite generation, NPC/CGB-Se images (b)
SEM, (c) TEM.[55]
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Figure 15. (a) Schematic illustration of the synthesis of CoP@C-RGO-NF, CoP@C-RGO-NF. (b) SEM
images of CoP@C-RGO-NF and (c) TEM image of CoP@C-RGO-NF.[56]