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Open AccessReview

Dealloying of Cu-Based Metallic Glasses in Acidic Solutions: Products and Energy Storage Applications

School of Materials Science and Engineering, Hebei University of Technology, Tianjin 300130, China
Key Laboratory for New Type of Functional Materials in Hebei Province, Hebei University of Technology, Tianjin 300130, China
CITIC Dicastal Co. Ltd., Qinhuangdao 066011, China
Authors to whom correspondence should be addressed.
These authors contributed equally to this work.
Academic Editor: Jiye Fang
Nanomaterials 2015, 5(2), 697-721;
Received: 4 February 2015 / Revised: 17 April 2015 / Accepted: 23 April 2015 / Published: 29 April 2015
(This article belongs to the Special Issue Nanomaterials for Energy and Sustainability Applications)


Dealloying, a famous ancient etching technique, was used to produce nanoporous metals decades ago. With the development of dealloying techniques and theories, various interesting dealloying products including nanoporous metals/alloys, metal oxides and composites, which exhibit excellent catalytic, optical and sensing performance, have been developed in recent years. As a result, the research on dealloying products is of great importance for developing new materials with superior physical and chemical properties. In this paper, typical dealloying products from Cu-based metallic glasses after dealloying in hydrofluoric acid and hydrochloric acid solutions are summarized. Several potential application fields of these dealloying products are discussed. A promising application of nanoporous Cu (NPC) and NPC-contained composites related to the energy storage field is introduced. It is expected that more promising dealloying products could be developed for practical energy storage applications.
Keywords: dealloying; metallic glass; nanoporous copper; energy storage; application dealloying; metallic glass; nanoporous copper; energy storage; application

1. Introduction

Dealloying, which is a well known etching technique, refers to selective dissolution of one or more components out of an alloy [1], leaving residual noble metal nanoporous structure. Such a technique, initially known as depletion gilding [2], has been used by metalsmiths to gold-coat artifacts for millennia, dating back to the Nagada period (prehistory 4000–3100 BC) [2]. However, some speculate that a nanoporous structure is formed during alloy corrosion owing to the limitation of observation at the nanoscale in the past. This idea has recently been receiving renewed attention because various dealloying products, including nanoporous metals, nanoporous alloys, metallic oxide and composites with excellent physical and chemical properties, can be fabricated by this method [3,4,5,6] and can be clearly observed using a high performance scanning electron microscope (SEM) and transmission electron microscopy (TEM), in recent decades [7]. As a result, research on products and applications of an alloy after dealloying has become a hot topic and is drawing increasing attention.
Nanoporous metals and alloys are known as easily obtained dealloying products after corrosion. With the development of dealloying techniques and theories, nanoporous metals such as Au [8], Pd [9], Pt [10], Ag [11] and Cu [12], as well as nanoporous alloys including Au–Ag [13], Pt–Ru [14], Pd–Ag [15] and Pt–Au [16] have been developed in the latest 15 years. They have been revealed for potential applications in catalysis [17], heat exchangers [18], actuators [19], energy storage [20], biosensors [21] and surface-enhanced Raman scattering [22]. Besides this applied research, some basic research related to dealloying has been carried out. Erlebacher and coworkers [23] proposed an atomistic model to explain the formation mechanism of the nanoporous structure during dealloying. Delogu’s group [24] developed theoretical models to relate structure and mechanical properties in nanoporous metals. Hosson et al. [25,26] studied strain in nanoporous gold. Biener [27], Lian [28] and Weissmüller et al. [29] studied mechanical properties of nanoporous metal and composites. It was found that after mixing nanoporous gold with epoxy, the composite became stronger and harder than each constituent phase individually. Thus, as a kind of engineering material, the application field of nanoporous metal can be extended. However, extensive studies have focused on the fabrication and properties of nanoporous noble metals and alloys. Research pertaining to inexpensive nanoporous metals and other fascinating dealloying products is quite rare. As we know, the cost must be taken into account for practical commercial application of the dealloyed products. Recently, a new series of dealloyed products including nanoporous Cu (NPC) and nano/micro-Cu oxides with low cost and unique properties have been developed in our group [30,31,32,33,34]. This paper presents an overview of our recent advancement of dealloyed products via free-dealloying Cu-based metallic glasses (MGs) in hydrofluoric acid (HF) and hydrochloric acid (HCl) solutions, as well as a brief review of others’ results related to dealloying. The prospective potential applications of the dealloyed NPC and composites are also introduced.

2. Fabrication of NPC

The fabrication of inexpensive NPC has attracted the attention of numerous researchers. Many direct factors, such as alloy composition, dealloying solutions, etching time, dealloying temperatures and electrochemical potential, have been widely studied [35,36,37,38,39]. These factors are confirmed to influence the specific structural characteristics of the NPC.
Based on a large number of experiments, the microstructure and chemical composition of a precursor alloy are the key parameters to determine the dealloying process and the morphology of nanopores. To prepare uniform nanoporous metal, a homogeneous single phase of dealloying precursor is necessary. Due to their single phase nature, representative single phase solid solution and metallic glasses are good candidates as dealloying precursors. For example, Au–Ag alloy [40] is an ideal and classical precursor to produce uniform nanoporous Au by selectively dissolving the constituent element Ag, because Au and Ag are completely miscible through the entire composition range and no phase separation occurs during the dealloying process. For two-phase or multiphase alloy systems, however, the dealloying results are complicated. In the case of a two-phase system, if one phase can be removed from the alloy and another remains, porous/nonporous metal composites can be fabricated. If the dealloying takes place within each phase, then nanoporous metal composite with two kinds of nanoporous metals or two different pore size distributions can be obtained [41,42]. Up to now, Mn–Cu [43], Al–Cu [44], Mg–Cu [45] and Zn–Cu [46] crystalline precursors have been used to produce NPC with different porous structures. Aside from crystal precursors, recently, amorphous materials such as MGs have also been demonstrated to be a new type of precursor for dealloying to nanoporous metals. MGs are known for their chemically homogeneous single-phase nature which lack crystalline defects and large-scaled phase segregations. They have thousands of compositions and can be used to fabricate various nanoporous metals which cannot be achieved from conventional crystalline precursors. Nowadays, MG precursors including Ti–Cu(–Au) [47,48], Mg–Cu–Y [49], Mg–Cu–Gd [50], Cu–Zr–Ti [51], Cu–Hf–Al [30], Cu–Zr(–Al) [31] and Al–Cu–Mg(–Ni) [52] have been used to obtain uniform NPC through chemical/electrochemical dealloying processes. As shown in Figure 1, a NPC ribbon, which obtained by dealloying of Cu–Hf–Al MGs [30], presented a typical three-dimensional (3D) continuous nanoporous structure. For a binary MG, different atomic ratios influence the pore size of the resulting 3D nanoporous structure. For example, as atomic ratios of the Cu in Ti–Cu ribbons increased, the pore size of NPC decreased [47]. Moreover, the ligament/pore size of dealloyed NPC can be tailored by the addition of different third components into binary MGs. For instance, the pore size of NPC dealloyed from the Ti60Cu39Ag1 alloy was smaller than that of the Ti60Cu40 alloy [53]. A noble Au additive in Ti–Cu MGs resulted in the formation of an NPC with ultrafine nanoporous structure [48]. An active Al additive in Cu–Zr MGs, however, led to the formation of a wider ligament of dealloyed NPC [31].
For dealloying study, a proper etching solution must be correctly selected. For obtaining NPC using a dealloying method, the constituent elements of the precursor alloy exhibiting a large difference in the galvanic series [54] in an etching solution is a necessary requirement. Figure 2 shows open-circuit potentials vs. time curves of the metal Cu, Hf and Al in 0.5 M HF solution at 298 K open to air. Among the constituent elements, Cu metal shows much higher stability in HF solution due to its much nobler potential, whereas Hf and Al metals exhibit high electrochemical activity. It can be also seen from Figure 2 that the potential differences between Cu and other two elements are noticeable and greater than 0.8 V, which provides an advantageous driving force for the dissolution of less noble elements Hf and Al under free corrosion conditions. As a result, a uniform NPC can be obtained by dealloying the Cu52.5Hf40Al7.5 MG in 0.5 M HF solution [30]. Various corrosive solutions, such as HCl [55], H2SO4 [56], HF [57], H3PO4 [58] and HBF4 [59] solutions, NaOH aqueous alkali [60] and NaCl saline solution [61], were successfully used to produce NPC. Representative NPC obtained by dealloying of MGs in different electrolytes is listed in Table 1.
Figure 1. Typical nanoporous Cu (NPC) obtained by dealloying of Cu52.5Hf40Al7.5 MGs in 0.5 M hydrofluoric acid (HF) solution for 300 s [30]. (a) Scanning electron microscope (SEM) image; (b) Transmission electron microscopy (TEM) image.
Figure 1. Typical nanoporous Cu (NPC) obtained by dealloying of Cu52.5Hf40Al7.5 MGs in 0.5 M hydrofluoric acid (HF) solution for 300 s [30]. (a) Scanning electron microscope (SEM) image; (b) Transmission electron microscopy (TEM) image.
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Figure 2. Open-circuit potentials of metals Cu, Hf and Al in 0.5 M HF solution at 298 K open to air [30].
Figure 2. Open-circuit potentials of metals Cu, Hf and Al in 0.5 M HF solution at 298 K open to air [30].
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Table 1. Representative NPC obtained via dealloying of MGs.
Table 1. Representative NPC obtained via dealloying of MGs.
Dealloying SolutionPrecursorsReferences
HClAl70Cu18Mg12, (Al75Cu17Mg8)97Ni3[52,62]
H2SO4Mg90−xCuxY10 (x = 20, 25, 30, 40 at.%)[49,56]
H2SO4 + PVPMg65Cu25Y10[12]
Cu50Zr50−xAlx (x = 0, 5 at.%)[31]
Ti100−xCux (x = 33, 40, 50, 60, 70 at.%)[47,63,64]
Ti–Cu–(Ag, Au, Ni, Pd, Pt)[48,53,57,65,66,67]
HF + PVPTi60Cu40[68]
Diverse acidic solutions have been widely used for dealloying to produce NPC. It was reported that the ligament/pore size of dealloyed NPC was strongly influenced by the corrosive solution. Generally, the length scale of the NPC ligament and pore size turned to be greater in more concentrated solutions [47]. In addition, an introduction of organic macromolecules into dealloying solution was conducive to refined nanoporous structures [12,68]. It was reported that the pore and ligament sizes decreased in a mixed solution of poly-vinylpyrrolidone (PVP) and sulfuric acid compared to those in the PVP-free H2SO4 solution. With increasing concentration of PVP in the dealloying solutions, the sizes of nanopores and ligaments decreased.
Besides the precursor composition and dealloying solution, etching conditions such as dealloying time and temperature also have great effects on the ligament/pore size of the nanoporous metals. Controlling etching conditions is a simple and effective way to tailor porous structures, which determines the final physical and chemical properties of the NPC. Since the dealloying takes place layer by layer, the thickness of the nanoporous metal increases with increasing the etching time. By choosing a proper etching time, we can produce a complete 3D nanoporous structure material without further coarsening of the ligament/pore. Meanwhile, inefficient dealloying of a MG precursor resulted in the fabrication of a nanoporous metal/MG/nanoporous metal composite with a sandwich-like structure [30]. The sandwich-like structure composites containing a MG ductile interlayer showed good bendability [30]. It was presented that the interplay between ligament width d of NPC and dealloying time t can be deduced [56] as:
ln d = 1 n ln t E n R T + 1 n ln ( K D 0 )
where n is the coarsening exponent, T is the temperature, E is the activation energy for the ligament growth, R is the gas constant, D0 and K are constants. According to the formula, a linear law between lnd and lnt can be established. In addition, the linear laws were revealed between logarithm of the pore sizes and logarithm of the dealloying time [57], as well as between logarithm of the ligament width and reciprocal of the dealloying temperature [48]. Generally, the ligament/pore size increases with the dealloying time/temperature. This corollary has been verified by some studies [22,56].
There are also some indirect factors to influence the microstructure of dealloyed nanoporous metals. These indirect factors include the parting limit (for most dealloying precursors, the critical range of the noble component in an alloy is between 20 and 60 at.%), the diffusivity of a noble metal at alloy/electrolyte interfaces, the critical potential (for the electrochemical dealloying), volume shrinks and surface cracks, and so on [69]. In general, the microstructure of nanoporous metals fabricated in dealloying process is influenced by many factors, which should be controlled carefully.

3. Synthesis of NPC/Metal Oxides Composites

The NPC/metal oxides composites integrate NPC and other functional metal oxides together. They can be created through various methods and have potential for application in different fields. Relatively active NPC obtained by dealloying can be easily oxidized into NPC/Cu2O or NPC/CuO composites by annealing in air [58,70]. It was found that heat treatments toward NPC between 200 and 600 °C led to the formation of Cu oxide (CuO and Cu2O) layers [58]. These oxide layers with a thickness of ten to dozens of nanometers can be produced on the surface of the 3D NPC via in situ thermal oxidation process. For NPC with relative density of 20%~30%, the oxide layers were mainly made up of Cu2O after annealing at 200 °C for 30 min, while those that were composed of CuO after annealing between 400 and 600 °C for 30 min. It was reported that the oxide layer growth thicknesses in a temperature range of 100~600 °C can be estimated using the following formula [58]:
d oxide ( t ) = A exp ( Q R × T ) × t 1 / 2 + d 0
where doxide(t) is the thickness of the formed copper oxide as a function of time, R is the gas constant, T is the temperature, t is time in minutes, A is the initial coefficient with values ranging from 5.518 × 105 to 6.658 × 107 Å·min−1/2, Q is activation energy and d0 is the initial copper oxide thickness. Thus, the thickness of Cu oxide film on the surface of NPC can be controlled by adjusting oxidation temperature and annealing time.
Ding and co-workers [71] revealed a general corrosion strategy for the straightforward fabrication of a variety of nano-structured metal oxide through a dealloying and spontaneous oxidation method. The approach mainly involves the alloying consisting of the targeted transition metals and more active metal species, and a subsequent selective leaching of active metals in proper etching liquid. During this corrosion process, the transition metal atoms left behind will undergo spontaneous oxidation at the metal/electrolyte interface to form metal oxides. By following this route, nano-structured Co3O4, Fe3O4, WO3, TiO2 and Mn3O4 with intricate structural properties have been successfully synthesized [5,71,72,73,74,75]. To develop this corrosion strategy, Zhang et al. [76] reported an attempt to dealloy Cu–Fe–Al ternary alloy in alkaline solutions. As a result, NPC/(Cu,Fe)3O4 composites were obtained by a direct one-step dealloying process. These composites were composed of a NPC matrix with ligament/channel sizes of 20–40 nm and octahedral (Fe,Cu)3O4 embedded particles 600–800 nm in size. The formation of these composites can be explained by the surface diffusion of Cu adatoms (to form a NPC matrix) and oxidation of the active Fe/Cu adatoms (to form metal oxides) during dealloying.
By drawing on Ding’s corrosion strategy [71], here we report a successful fabrication of a NPC/Cu2O composite using the oxygen-assisted dealloying method. Unlike in our previous study [30], the HF etching solution is replenished with oxygen during the dealloying process. Then, a part of active Cu adatoms can be smoothly oxidated to Cu2O nanoparticles. It can be seen in Figure 3a that the color of the ribbons before and after dealloying in oxygen-enriched 0.65 M HF solutions obviously changes. With the increase of the dealloying time, the ribbon color turns from argenteous to a typical Cu metallic luster and finally changes to dark red. During the dealloying with etching time from 0 to 420 s, the ribbons keep their mechanical integrity, which is important for the subsequent applications. Figure 3b shows X-ray diffraction (XRD) patterns of Cu52.5Hf40Al7.5 MGs dealloying in oxygen-enriched 0.65 M HF with different etching times. The diffraction pattern of the as-spun ribbon shows a characteristic broad halo peak without appreciable crystal phase, indicating a single homogeneous amorphous structure. The SEM image (Figure 4a) of the ribbon treated in 0.65 M HF for 180 s presents nanoporous structure. The XRD pattern of the ribbon exhibits sharp crystal peaks which match with (111), (200), (220) crystal planes of Cu (JCPDS No.04-0836). However, no remaining amorphous phase is recognized in the XRD pattern. It is indicated that most of the Hf and Al elements are selectively removed from the Cu–Hf–Al precursor alloy after dealloying in 0.65 M HF for 180 s, leaving much nobler Cu element behind. As a result, the as-obtained porous metal can be identified as NPC. When the dealloying time is prolonged to 300 s, it is observed that many Cu2O nanocubes are formed on surfaces of the NPC (Figure 4b). When the dealloying time reaches 420 s, more Cu2O nanocubes coat or embed into the NPC structure to form the NPC/Cu2O nanocube composite (Figure 4c). These are also verified by the increasing intensity of Cu2O peaks in Figure 3b. Moreover, it can be seen that the dealloying product exhibits a new nanoporous composite structure.
Figure 3. Macrophotograph (a) and X-ray diffraction (XRD) patterns (b) of the melt-spun Cu52.5Hf40Al7.5 ribbon before and after dealloying in oxygen-enriched 0.65 M HF for different time at 298 K open to air. Scale bar, 1 cm.
Figure 3. Macrophotograph (a) and X-ray diffraction (XRD) patterns (b) of the melt-spun Cu52.5Hf40Al7.5 ribbon before and after dealloying in oxygen-enriched 0.65 M HF for different time at 298 K open to air. Scale bar, 1 cm.
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From the above typical example, a general method to produce NPC/Cu2O composite structure is schematically illustrated in Figure 4d–i. The method is based on dealloying in an oxygen-enriched corrosive solution. Firstly, a 3D NPC is obtained in dealloying process. Secondly, a portion of copper on the surfaces of NPC ligaments reacts with dissolved oxygen to form Cu2O nanoparticles. Through the long dealloying process, a mass of Cu2O nanoparticles are formed on the surfaces of NPC ligaments by reaction between copper and oxygen. At last, a Cu2O particle layer with a certain thickness is formed on NPC surfaces. Thus, NPC/Cu2O composites exhibiting new nanoporous structure can be produced and can be further controlled by adjusting the dealloying time and the oxygen content in the etching solution. A similar method is also used to produce porous CuO nanoplate-films with an oxidation-assisted dealloying method [77]. It was observed that the Cu component in an alloy was oxidized preferentially into Cu2O nanocubes due to free oxidation by dissolved oxygen in electrolytes. Then, the Cu2O nanocubes are further oxidized into CuO nanoplates mainly owing to primary-cell-induced oxygen consuming corrosion. Such a method can be used universally to fabricate various porous metal oxide nanostructural films on flexible substrates for future nanostructure-based integrated circuit, sensor and solar cell applications.
Besides the above methods, NPC/metal oxides composites can also be synthesized through chemical deposition of metal oxides on prefabricated NPC. Recently, our group produced a new NPC-supported MnO2 composite (MnO2/NPC/MnO2 sandwich structure) [30]. We firstly synthesized a monolithic NPC ribbon with good mechanical integrity and bendability by designing a ductile MG-containing interlayer in the ribbon (Figure 5a). Then, the NPC was used as the substrate for the MnO2 deposition. It can be seen from Figure 5b that the as-obtained MnO2 prepared through the classical chemical reaction between KMnO4 and ethanol was composed of nanosized globular particles, which showed a serious particle aggregation phenomenon. By using a ductile NPC support, however, MnO2 nanoflakes (Figure 5c) were homogeneously deposited on the surface of the NPC substrate. This result indicated that the NPC with large specific surface areas and excellent electrical conductivity can effectively promote the morphological change of MnO2 from globular particles to nanoflakes for larger specific surface area and improve the utilization of MnO2 surface active sites. This method can be extended to develop more NPC/metal oxide composites with distinctive functional properties.
Figure 4. SEM (ac) and schematic images (di) of Cu52.5Hf40Al7.5 MGs dealloying in O-enriched 0.65 M HF with different time. (a,d,g) 180 s; (b,e,h) 300 s; (c,f,i) 420 s.
Figure 4. SEM (ac) and schematic images (di) of Cu52.5Hf40Al7.5 MGs dealloying in O-enriched 0.65 M HF with different time. (a,d,g) 180 s; (b,e,h) 300 s; (c,f,i) 420 s.
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Figure 5. Fabrication of NPC/MnO2 composite [30]. (a) Schematic of fabrication process; (b) as-prepared MnO2 powders; (c) NPC/MnO2 composite with 50 wt.% MnO2.
Figure 5. Fabrication of NPC/MnO2 composite [30]. (a) Schematic of fabrication process; (b) as-prepared MnO2 powders; (c) NPC/MnO2 composite with 50 wt.% MnO2.
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4. Synthesis of Cu2O Particles on Surface of MGs

So far as we know, Cu–Hf–Al MGs presented relatively good corrosion resistance in many electrolytes [78]. When dealloying Cu–Hf–Al MGs in different etching solutions, the dealloying products are diverse. As discussed in the last section, by dealloying Cu–Hf–Al MGs in 0.5 M HF solution, NPC as the general dealloying product can be fabricated. when dealloying Cu–Hf–Al MGs in HCl solutions, however, dealloying products are mainly Cu2O crystals with different and interesting morphologies, which are reviewed in this section. The reason why NPC cannot be produced in Cu–Hf–Al MGs by using HCl electrolytes can be explained as follows. The corrosion rates of the Cu52.5Hf40Al7.5 MG both in 0.5 M HCl and 0.5 M HF solutions can be estimated using the following formula [79]:
R = 87600 Δ w s ρ t
where R is corrosion rate (mm·y−1), Δw is weight loss (g), s is surface area of specimen (cm2), ρ is density of specimen (g·cm−3) and t is immersion time (h). This shows that the corrosion rate of the Cu52.5Hf40Al7.5 MG in 0.5 M HCl solution is about 0.2 mm·y−1, while it is more than 500 mm·y−1 in 0.5 M HF electrolyte [80]. Consequently, it is very difficult to etch Cu52.5Hf40Al7.5 MGs in HCl solution. On the other hand, Cu, Hf and Al elements showed noticeable potential difference in HF electrolytes, while the potential difference is small in HCl solution. For example, the potential difference between Cu and Hf in 0.5 M HF electrolytes was distinct and more than 0.8 V, which provides an advantageous driving force for the dissolution of less noble elements Hf under free corrosion condition. The potential difference between Cu and Hf in 0.5 M HCl solution, however, was less than 0.2 V [80]. Thus, it is difficult to remove Hf in HCl solution under free etching conditions. Considering the above two aspects, NPC cannot be easily synthesized by dealloying of Cu–Hf–Al MGs in HCl electrolytes.

4.1. Synthesis of Regular Cu2O Particles on Surface of MGs

Xue et al. [81] found that Cu2O, the initially formed product of Cu oxidation in air or oxygen atmosphere, can spontaneously grow at the surface of Cu foil in Cl solutions at room temperature. By adjusting concentrations of Cl ions, Cu2O crystals with various shapes including octahedra, rhombic dodecahedra and spheres are produced and can be tailored on the surface of Cu foil. Using the salutary experience of this route, we found that various and regular Cu2O particles can also be fabricated on surfaces of MGs by dealloying Cu-based MG ribbons in the HCl solution with low concentrations for different times. For example, by dealloying Cu52.5Hf40Al7.5 MG ribbons in 0.05 M diluted HCl solution for 4 h, 5 h, 6 h, 8 h, 14 h, 20 h and 24 h, Cu2O crystals with truncated tetrahedron, cube, cuboctahedron, truncated octahedron, octahedron, hexapod and octahedron-detached hexapod shapes [32,33] were synthesized, respectively. So, regular Cu2O particles with designable morphology can be tailored in the diluted HCl solution by simply controlling dealloying time.
The characteristics of these regular Cu2O crystals are listed in Table 2. It can be seen that the 3D sizes of Cu2O crystals do not change much in the first 8 h of dealloying though they show different edge lengths. Then, the sizes of Cu2O crystals increase obviously after dealloying for 14 h, and get bigger with the increase in dealloying time. It should be noted that the volume fraction of Cu2O particles on MG surface is low (less than 20%) and does not change much with the extension of etching time. Since the Cu2O crystals with different morphologies possess important electrical and optical properties [82,83], it is necessary to enhance the volume fraction of Cu2O particles on the glassy surface.
Table 2. Characteristics of regular Cu2O crystals produced by free dealloying of Cu52.5Hf40Al7.5 MG in 0.05 M HCl solution for different times at 298 K open to air [32,33].
Table 2. Characteristics of regular Cu2O crystals produced by free dealloying of Cu52.5Hf40Al7.5 MG in 0.05 M HCl solution for different times at 298 K open to air [32,33].
Dealloying Time/h4568142024
Morphology Nanomaterials 05 00697 i001 Nanomaterials 05 00697 i002 Nanomaterials 05 00697 i003 Nanomaterials 05 00697 i004 Nanomaterials 05 00697 i005 Nanomaterials 05 00697 i006 Nanomaterials 05 00697 i007
Truncated tetrahedronCubeCuboctahedronTruncated octahedronOctahedronHexapodsOctahedron-detached hexapods
Edge length/nm~300~300~300~150~450~500~1100
Volume fraction/%10.613.312.213.915.814.419.8 (mixed with other shapes)

4.2. Preparation of Cu2O Micro-flowers on Surface of MGs

In order to improve the volume fraction of Cu2O particles on glassy surfaces, Cu-based MG ribbons dealloying in HCl solutions with enhanced concentration were studied [34]. After Cu52.5Hf40Al7.5 glassy ribbons were dealloyed in 0.1 M, 0.2 M and 0.4 M HCl solution for 8 h, Cu2O particles formed on MG surfaces exhibited a flower-like shape. The mean surface coverage rate of Cu2O micro-flowers increased from 17.2% to 33.1% with the increase in HCl concentration. The Cu2O coverage rate was improved compare with the above work (13.9%, 0.05 M HCl for 8 h) [32]. The improvement in the Cu2O coverage rate arose from the increased HCl concentration that promoted the dealloying reaction including the reaction speed and reaction product. As a result, the sizes of Cu2O crystals gradually increased and Cu2O crystals in regular polyhedral shapes could not be maintained but rather grow into micro-flowers. On the other hand, Cu52.5Hf40Al7.5 glassy ribbons dealloying in 0.5 M HCl solution for 8 h, 14 h and 20 h were also studied [34]. When the dealloying time was extended from 8 h to 14 h, some cracks were formed on the glassy surface. Furthermore, deeper cracks were observed in the ribbon surface dealloyed for 20 h. It was found that plentiful Cu2O/CuO particles grew up from these crack walls. With the increase of the dealloying time, the mean surface coverage rate of CuxO (x = 1,2) crystals increased gradually.
From the above results, we can conclude that higher concentration of HCl solutions and longer dealloying time are beneficial for improving the volume fraction of Cu2O particles on glassy surfaces. However, the cracks formed on the Cu–Hf–Al glassy surfaces in concentrated HCl solutions are unavoidable. They are harmful to the mechanical integrity of an alloy ribbon. To solve this problem, dealloying attempts to Cu–Hf–Al–Nb glassy ribbons are made. For Cu52.5Hf40Al7.5 glassy ribbon dealloying in 1.2 M HCl for only 1.5 h (Figure 6a,b), many cracks form on the ribbon surface. Cu2O micro-flowers with diameter about 600 nm grow up from the crack walls. For Cu52.5Hf40Al5Nb2.5 glassy ribbon dealloying in 1.2 M HCl for 14 h (Figure 6c,d), dimples instead of cracks are present on the ribbon surface. Cu2O micro-flowers with the biggest size to 1.1 μm grow along the edges of the dimples. For Cu50Hf40Al5Nb5 glassy ribbon dealloying in 1.2 M HCl for 14 h (Figure 6e,f), however, a smooth surface is retained. Cu2O micro-flowers with diameter less than 700 nm are created on the glassy surface. The volume fraction of Cu2O crystals on glassy surfaces reaches 39% ± 5 %. Thus, a composite with an ideal glassy surface plus a relatively high volume fraction of Cu2O micro-flowers is successfully synthesized.
Figure 7 shows potentiodynamic polarization curves of Cu–Hf–Al(–Nb) glassy ribbons in 1.2 M HCl solution. With the increase of the Nb content, MG samples present lower corrosion current density and more positive corrosion potential, indicating a big improvement in the corrosion resistance of the MG samples. So, Cu50Hf40Al5Nb5 glassy ribbon with good corrosion resistance in 1.2 M HCl solution can maintain its smooth surface during the long corrosion process. To our knowledge, MG is a good carrier for Cu2O particles, because MG exhibits high strength, high toughness and high corrosion resistance. In addition, the Cu2O crystals formed on MG surfaces are easier to store or extract as compared to traditional chemical methods. Consequently, the MG/Cu2O micro-flower compounds contain multiple potential properties which are well worth developing.
Figure 6. SEM images of Cu-based MG dealloying in 1.2 M HCl solution at 298 K. (a,b) Cu52.5Hf40Al7.5 MG, dealloying for 1.5 h; (c,d) Cu52.5Hf40Al5Nb2.5 MG, dealloying for 14 h; (e,f) Cu50Hf40Al5Nb5 MG, dealloying for 14 h.
Figure 6. SEM images of Cu-based MG dealloying in 1.2 M HCl solution at 298 K. (a,b) Cu52.5Hf40Al7.5 MG, dealloying for 1.5 h; (c,d) Cu52.5Hf40Al5Nb2.5 MG, dealloying for 14 h; (e,f) Cu50Hf40Al5Nb5 MG, dealloying for 14 h.
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Figure 7. Potentiodynamic polarization curves of Cu–Hf–Al(–Nb) MG in 1.2 M HCl solution at 298 K open to air.
Figure 7. Potentiodynamic polarization curves of Cu–Hf–Al(–Nb) MG in 1.2 M HCl solution at 298 K open to air.
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Dealloying products of Cu-based MG ribbons in HF and HCl solutions are summarized in Table 3. By choosing different Cu-based MGs and etching conditions, various dealloying products with different surface and inner compositions can be tailored. These dealloying products with multiple functionalities could be applied in wide fields in near future.
Table 3. Summary of dealloying products of Cu-based MG in acidic solutions at 298 K.
Table 3. Summary of dealloying products of Cu-based MG in acidic solutions at 298 K.
Etching SolutionDealloying ProductsMGDealloying ConditionsReferences
HFNPCNPCCu52.5Hf40Al7.50.5 M HF, 300 s[30]
NPCRegular Cu2O particlesCu52.5Hf40Al7.5oxygen-enriched 0.65 M HF, 420 sThis study
HClMGRegular Cu2O particlesCu52.5Hf40Al7.50.05 M HCl, 4~24 h[32,33]
MGCu2O micro-flowersCu50Hf40Al5Nb51.2 M HCl, 14 hThis study

5. Applications of Dealloying Products

The paper reviews representative dealloying products of Cu-based MGs in acidic solutions, such as NPC, NPC/Cu2O composites and metallic glass-supported Cu2O composites with tunable Cu2O shapes. These new dealloying products with unique structures and multiple properties would provide a wide array of possible applications in many areas.
Nanoporous metals, as the most famous dealloying products, have been the focus of much attention due to their potential in various applications. So far, the study on nanoporous gold (NPG) makes up a high proportion of dealloying works. Just in recent years, fabrication and application development of inexpensive NPC have attracted considerable attention from many researchers. Representative applications of NPC and composites are listed in Table 4. The first significant development toward NPC was reported by Chen’s group [22]. It was found that the tunable nanoporosity leads to a remarkable improvement in surface-enhanced Raman scattering (SERS) of NPC, which was helpful in developing inexpensive SERS substrates for sensitive instrumentations in molecular diagnostics. After that, diversified reports about NPC applications were unveiled. For example, NPC was considered to be a good support for horseradish peroxidase immobilization [84]. Moreover, NPC-contained composites presented superior catalytic and sensitive performance in oxidation of hydrazine and alcohols, degrading organic compounds and detecting glucose [50,85,86,87,88].
Table 4. Representative applications of NPC and composites.
Table 4. Representative applications of NPC and composites.
ProductsApplication FieldReferences
NPCSurface-enhanced Raman scattering (SERS)[22,89]
Immobilization of horseradish peroxidase[84]
NPC/Ag core–shell compositeSERS[90]
NPC/Pt(Pd) core–shell compositeMethanol electro-oxidation[91]
NPC/Au core-shell compositeElectrocatalysis and nonenzymatic biosensing[87]
Ni-B amorphous nanoparticles modified NPCEthanol oxidation[88,92]
NPC/Cu compositeElectro-oxidation of hydrazine[85]
Nanoporous Cu–O systemCatalysts towards CO oxidation[93]
NPC/Cu2O nanocompositeAdsorption of methyl orange[94]
NPC/MG compositeDegradation of azo dye[86]
Degradation of phenol[50]
NPC/Si compositeLithium-ion battery anodes[95]
NPC/Cu2O composite[70]
Cu/NPC/MnO2 composite[96]
NPC/MnO2 compositeSupercapacitor electrodes[30]
NPC/(Fe,Cu)3O4 compositesExcellent magnetic/electrical properties for potential applications in sensors, information storage, and so on[76]
Besides these developments, an important application field for NPC is energy storage, especially for electrochemical supercapacitors (ECs). As charge-storage devices, ECs possess a unique combination of high power, high energy and long lifetimes [97,98]. They were widely used in portable electronics and hybrid electric vehicles [99,100]. There are two basic kinds of ECs: one is double-layer capacitance relying on surface ion adsorption, such as carbon based materials (e.g., carbon nanotubes, graphene, porous carbon, carbon aerogel and active carbon fiber) [101,102,103,104,105]; another is pseudo-capacitance relying on surface redox reactions, including metal oxides (e.g., RuO2, MnO2, Co3O4 and NiO) [106,107,108,109] and conducting polymers (e.g., polyaniline, polypyrrole and polythiophene) [110,111,112]. It should be noted that the capacitive performances of ECs depend on the effective surface area and conductivity of electrode materials [98]. Thus, NPG with a high specific surface area and high conductivity has been firstly tried as a current collector or a substrate support for the electrode materials in supercapacitors. It was reported that bare NPG-based double-layer supercapacitors had excellent charge-discharge cycling stability, although their capacitance was still too low (~5 F·g−1) for real applications [113,114]. For enhancing capacitive performance, pseudo-capacitive materials with high theoretical values such as MnO2, polyaniline and polypyrrole (PPy) were deposited on the high-surface-area and highly conductive NPG surface [115,116,117]. These nanocomposite-based supercapacitors exhibit high capacitance properties (e.g., a specific capacitance of ~1145 F·g−1 for NPG/MnO2, a power density of 296 kW·kg−1 for NPG/PPy). However, Au is a well-known noble metal, which would limit its large-scale application. With the aim of reducing the cost and promoting the practical application of nanoporous metals in the EC field, nanoporous Ni has been fabricated by dealloying Mn–Ni, Al–Ni, Cu–Ni, Fe–Ni, Mg–Ni, Zn–Ni and Mn–Ni–Cu alloy in different solutions [118,119,120,121]. The nanoporous Ni as an electrode substrate presented a stable areal capacitance (1.7 F·cm−2) [122]; however, a very small pore size (usually less than 10 nm) inhibited the growth of the pseudo-capacitive materials inside the nanopores. Therefore, it is expected that the inexpensive nanoporous Cu (NPC) with tunable pore size in a wide range from 10 to 60 nm could be considered as an excellent substrate support for pseudo-capacitive materials.
In our recent work, a new NPC-supported MnO2 (NPC/MnO2) composite for ECs was produced [30]. It can be clearly seen from the cyclic voltammogram (CV) curves (Figure 8a) that the capacitive current of the NPC in the voltage window was negligibly low, indicating NPC was only used as a stable substrate. On the other hand, it was surprisingly found that the closed area of CV curves (Figure 8a) and the specific capacitance values (Figure 8b) of the NPC/MnO2 composite were remarkably enhanced as compared to that of the pure MnO2 powders. When combining the electrochemical performance of pure MnO2 and NPC/MnO2 composites with their corresponding surface morphologies and distribution of MnO2 (Figure 5b,c), it was indicated that NPC substrate can efficiently improve the utilization of MnO2 surface active sites and promote MnO2 chemical reactions. The cycling stability of NPC/MnO2 composites with different weight ratios is presented in Figure 8c. The specific capacitance for the two composites remained greater than 97% and 82% of the initial value after 500 and 1000 cycles, respectively. All the results showed that the as-obtained NPC/MnO2 composite had a commendable potential for EC application. In future works, the optimization of the coated capacitive materials, including their amount and structure, could further enhance their capacitive performance and accelerate these inexpensive ECs for a practical application.
Figure 8. NPC/MnO2 composite for ECs. (a) CV curves of monolithic NPC, pure MnO2 and NPC/MnO2 composites with different weight ratios in 0.5 M Na2SO4 solution; (b) specific capacitance of monolithic NPC, pure MnO2 and NPC/MnO2 composites with different weight ratios; (c) cycling performance of the NPC/MnO2 composite at the scan rate of 10 mV·s−1; the inserts show CV curves of NPC/MnO2 composites with different weight ratios in 0.5 M Na2SO4 solution at different scan cycles. Adapted with permission from Elsevier, Copyright 2015 [30].
Figure 8. NPC/MnO2 composite for ECs. (a) CV curves of monolithic NPC, pure MnO2 and NPC/MnO2 composites with different weight ratios in 0.5 M Na2SO4 solution; (b) specific capacitance of monolithic NPC, pure MnO2 and NPC/MnO2 composites with different weight ratios; (c) cycling performance of the NPC/MnO2 composite at the scan rate of 10 mV·s−1; the inserts show CV curves of NPC/MnO2 composites with different weight ratios in 0.5 M Na2SO4 solution at different scan cycles. Adapted with permission from Elsevier, Copyright 2015 [30].
Nanomaterials 05 00697 g008
In NPC/MnO2 composite supercapacitor electrodes, the NPC, as a current collector, was the support for MnO2 nanoparticles. The presence of NPC changed the morphology of MnO2 and improved the utilization of surface active sites of MnO2. This is of great significance to develop electrode materials with high electrochemical performance. On the other hand, it is known that NPC is unstable and has a tendency to form Cu2O and CuO under high voltage. Using this, Cu/Cu2O composites [123,124] and Cu/CuO composites [125] were successfully developed for pseudocapacitance electrodes. The pseudocapacitance effect of these composites came from the redox transformation between the Cu+ and Cu2+ species in the process of charging and discharging. As a result, the synergistic effect of Cu oxide and MnO2 contributed to the pseudocapacitance properties of the composites, showing a low cost method for improvement of pseudocapacitance properties. Moreover, in comparison with carbon-based supercapacitor, the NPC-based supercapacitor exhibits distinct merits. Although carbon is a kind of low cost material and exhibits ultra-high specific capacitance, the production of carbon nanotubes, graphene, etc. includes a complex preparation process, expensive equipment, and low yield. Thus, it is difficult to achieve mass production of carbon-based supercapacitors at low cost. In contrast, the preparation of NPC is based on free dealloying, which is a very simple and rapid fabrication method. That makes NPC-based supercapacitors economical and practical. As a result, the development of NPC-based supercapacitors with low cost, stable properties and long lifetimes is of great importance.
An NPC used in lithium-ion batteries is another energy storage material. The fabrication of nanoporous metal-based composites for lithium-ion batteries is still in its early stages. Lang’s team [96] uncovered a flexible Cu/NPC/MnO2 hybrid bulk electrode for high-performance lithium-ion batteries, which showed a capacity as high as ~1100 mA·h·g−1 for 1000 cycles. In addition, it was reported that an NPC supported cuprous oxide prepared by the direct oxidation of NPC at high temperatures was applied in high-performance lithium ion battery anodes [70].
Up to now, the majority of research about applications of Cu-containing alloys for dealloying products has focused on NPC and NPC-based composites. Application development in broader fields for other dealloying products, such as NPC/Cu2O composites and MG/Cu2O composites with tailored Cu2O shapes, needs to be carried out in the near future. The corresponding experimental results will be presented soon by our group.

6. Conclusions and Outlook

The fabrication and applications of nanoporous metals and composites with dealloying techniques have earned more and more attention from academic research. These dealloying products show good performance in many fields. Although the history of research into dealloying is very short, the achievements gained in such a short period of time are amazing. According to the data from the “Web of Science” website (Figure 9), there have been 852 papers published in the dealloying field in the last 10 years (1 January 2004–31 March 2015). Every paper is cited nearly 20 times. In addition, the “H-index” is 63, which is far above average. The number of published papers and citations has risen over the last several years. In 2014, there were more than 150 published papers and over 4000 total citations. All the statistics show dealloying studies to be a hot topic in academia. As for papers published in countries/territories, the number of papers related to dealloying published by China, the USA, Japan and Germany is significantly higher than those of other countries/territories. In particular, papers in China account for more than forty percent. Per organization, Shandong University and Tohoku University, as leaders in the study of dealloying, have published the most papers in the world. The popularity of study in the dealloying field is thanks to rapid developments in the fields of energy, catalysis, biosensing, etc. Dealloying has become a multidisciplinary and interdisciplinary research. Dealloying research is also attracting more and more researchers from different disciplines. With sufficient cooperation, there will be more surprises in the near future.
Figure 9. Analyses of publications in the dealloying field using the topic of “dealloying” (1 January 2004–31 March 2015). (a) Papers published in each year; (b) citations in each year; (c) pie chart showing the paper publication ratio of different countries/territories; (d) bar graph showing the paper publication ratio of different organizations.
Figure 9. Analyses of publications in the dealloying field using the topic of “dealloying” (1 January 2004–31 March 2015). (a) Papers published in each year; (b) citations in each year; (c) pie chart showing the paper publication ratio of different countries/territories; (d) bar graph showing the paper publication ratio of different organizations.
Nanomaterials 05 00697 g009
In this paper, the dealloying products via free-dealloying of Cu-based metallic glasses in acid solutions are summarized. With different dealloying conditions, various dealloying products including NPC, NPC/Cu2O composites and MG/Cu2O composites are fabricated. NPC with uniform pore structure can be obtained by dealloying because of homogeneous structure of MG precursors. The ligament/pore size of dealloyed NPC can be tailored by the addition of different trace elements into MGs. A noble element such as Ag additive in MGs results in the formation of a nanoprous Cu–Ag alloy with ultrafine porous structure. An active element such as Al additive, however, leads to the formation of a wider ligament of NPC. Besides alloy compositions, many factors, such as dealloying solutions, etching time, dealloying temperatures and so on, have significant influence on the ligament/pore size of the resulting NPC. The change in ligament/pore size will influence the performance of the NPC in many application fields. Consequently, the application properties of NPC can be tailored by simply changing these factors. In addition, when dealloying in an oxygen-enrichment solution, metal oxide can be formed. In this study, NPC/Cu2O composites are synthesized by this method, which is called the dealloying and spontaneous oxidation method. The electrochemical properties of the composites need to be further developed. Meanwhile, MG presents excellent corrosion resistance performance in an appropriate corrosion environment. In this situation, MG ribbon with good mechanical integrity can be retained after corrosion, which provides an opportunity for the formation of MG-based compounds. The application fields of these compounds deserve to be further studied.
Energy storage is one of the most important and meaningful application fields of dealloying products. NPC possesses excellent electrical conductivity, and can be used as a current collector and support material for metal oxide. Thus, the as-obtained NPC/metal oxide composite material can be used as a low-cost supercapacitor and lithium ion battery electrodes. Through the combination of dealloying with other pore-forming technology, nano/mirco-porous Cu or so called bimodal porous Cu can be prepared. This type of composite with porous structure is expected to have a more outstanding performance in the field of energy storage. In lithium-air batteries, for example, the big pores can accommodate more discharge product (Li2O2) to enhance the energy density, while the small ligament/pore with high catalytic activity can effectively catalyze the reduction of Li2O2 into Li during the charge process to enhance the cycling stability [98]. At the same time, the porous structured composite can be used as a substrate to form nano/micro-scaled metal oxides with different morphologies using diverse techniques, such as anodization, heat treatment, chemical deposition and so on. The series of compounds are expected to show improved performance in energy storage.


The authors would like to acknowledge the financial support from both the “100 Talents Project” of Hebei Province, China (E2012100009), the Youth Fund of Key Laboratory for New Type of Functional Materials in Hebei Province, China (201503) and the Natural Science Foundation of Hebei Province, China (E2015202081).

Author Contributions

Zhifeng Wang and Chunling Qin designed this study and wrote the paper; Zhifeng Wang and Jiangyun Liu carried out the experiments and analyzed the data; Hui Yu, Xingchuan Xia, Chaoyang Wang, Yanshan Zhang, Qingfeng Hu and Weimin Zhao performed auxiliary operations in experiments. All authors discussed the results and commented on the manuscript.

Conflicts of Interest

The authors declare no conflict of interest.


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