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Article

Preparation of Amine-Modified Cu-Mg-Al LDH Composite Photocatalyst

by
Qining Wang
1,2,
Quanwang Yan
2,3,
Yu Zhao
2,4,
Jie Ren
3 and
Ning Ai
3,*
1
National Demonstration Center for Experimental Chemistry and Chemical Engineering Education, Zhejiang University of Technology, Hangzhou 310014, China
2
College of Chemical Engineering, Zhejiang University of Technology, Hangzhou 310014, China
3
School of Biology and Chemical Engineering, Jiaxing University, Jiaxing 314001, China
4
Sinochem Lantian Trading Co., Ltd., Hangzhou 310051, China
*
Author to whom correspondence should be addressed.
Nanomaterials 2022, 12(1), 127; https://doi.org/10.3390/nano12010127
Submission received: 17 November 2021 / Revised: 18 December 2021 / Accepted: 28 December 2021 / Published: 30 December 2021
(This article belongs to the Special Issue Transition Metal Complexes and Nanomaterials for Catalysis Application)
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Abstract

:
Cu-Mg-Al layered double hydroxides (LDHs) with amine modification were prepared by an organic combination of an anionic surfactant-mediated method and an ultrasonic spalling method using N-aminoethyl-γ-aminopropyltrimethoxysilane as a grafting agent. The materials were characterized by elemental analysis, XRD, SEM, FTIR, TGA, and XPS. The effects of the Cu2+ content on the surface morphology and the CO2 adsorption of Cu-Mg-Al LDHs were investigated, and the kinetics of the CO2 adsorption and the photocatalytic reduction of CO2 were further analyzed. The results indicated that the amine-modified method and appropriate Cu2+ contents can improve the surface morphology, the increase amine loading and the free-amino functional groups of the materials, which were beneficial to CO2 capture and adsorption. The CO2 adsorption capacity of Cu-Mg-Al N was 1.82 mmol·g−1 at 30 °C and a 0.1 MPa pure CO2 atmosphere. The kinetic model confirmed that CO2 adsorption was governed by both the physical and chemical adsorption, which could be enhanced with the increase of the Cu2+ content. The chemical adsorption was suppressed, when the Cu2+ content was too high. Cu-Mg-Al N can photocatalytically reduce CO2 to methanol with Cu2+ as an active site, which can significantly improve the CO2 adsorption and photocatalytic conversion.

1. Introduction

Uncontrolled burning of fossil fuels, since the industrial revolution, has not only caused serious energy consumption problems, but also made global warming an urgent problem for human sustainable development due to the sharp increase of CO2 concentration in the atmosphere [1,2,3]. For this reason, capturing CO2 from sources and converting it to carbon-containing fuels or high-value non-fuel chemicals are currently relatively attractive solutions to avoid extreme climate change [4,5]. As an extensively studied family of solid adsorbent, layered double hydroxides (LDHs) can realize the coupling of CO2 capture and utilization. Because LDHs materials have attractive physiochemical properties, such as characteristic layered structures with large surface areas, specific “memory effects”, high anion exchange capacity, precise morphological controllability, facileness to synthesize, and low costs [6,7,8,9,10,11].
Despite these positive properties, unactivated LDHs exhibit unstable structures and relatively low CO2 adsorption capacities in the range of 0.1 to 0.49 mmol·g−1 [12,13,14]. It is easy for substrates or reactants to penetrate the interlayer space, given the more defective and porous nature of the interlayer space for unactivated LDHs. It was proposed that the high stability comes from the less defective particle surface and the highly dense interlayer structure and manifested as a considerably higher crystallinity and a layer charge density [15]. Bond lengths, cell angles, electronic structure of cations, and the Mulliken population of clusters play a significant role in relative stability of LDHs [16]. In order to improve the structural stability and CO2 capture capacities, many attempts have been made, such as various synthesis approaches [17,18], modification of composition [19,20,21], morphology controlling [22,23], doping LDHs with alkali metal [24], and the formation of hybrid materials [25]. Enhanced capacities can be obtained by intercalating amino acids or amino silanes into stable layers and reacting with hydroxyl groups on laminates to achieve an amine loading. In light of the promising amine loading of intercalated LDHs, our research group proposed an amine-modified method [26,27], namely ultrasonic spalling [28] after co-precipitation [29], to further improve the adsorption performance of CO2.
LDHs, as excellent photocatalytic materials [30,31], have been applied in CO2 capture and conversion into small-molecular organic compounds such as CH4, CH3OH, and C2H5OH by photocatalytic reaction [32,33,34,35]. A series of LDHs can serve as sacrificial hard templates by host–guest structural design and assembly [36], of which the characteristic band gap can be adjusted with a wide choice of interlayer anions and metal cations [37]. LDHs, integrated with metals-bearing, high electron storage capacity and electron transportation efficiency [38,39], have great potential to enhance photocatalytic activity on the basis of the high adsorption capacity of CO2. Hong et al. [40] determined that the Mg-Al LDH, due to its excellent CO2 adsorption capacity, contributes to a remarkably high photocatalytic reduction efficiency of CO2 to CH4 in the presence of the carbon nitride (C3N4) photoabsorber and the Pd cocatalyst. The results show that the CH4 production of the Mg–Al LDH is 2.6 times that without the LDH coating and better than that of the Zn-Al LDH, the Ni-Al LDH, and the Zn-Cr LDH. Research on LDHs has extended from simple bicationic to tricationic or tetracationic multiphased species [41,42], of which the photocatalytic performances vary with the doping of different metal cations. Ahmed et al. [43,44] reported for the first time that LDHs can be applied as photo-catalysts to convert gaseous CO2 under UV-visible light using hydrogen. Compared with CO formed by Zn-Al LDHs, methanol is the major product formed by the inclusion of Cu sites using Zn-Cu-Ga LDHs, which suggested that the specific interaction of Cu sites with CO2 enables the formation of methanol by coupling with protons and photogenerated electrons. The efficient photocatalytic conversion of CO2 into methanol can also be observed over Zn-Cu-Ga LDHs by Morikawa et al. [45] in the preparation of reverse fuel cells.
The inclusion of Cu sites in LDH layers can improve the methanol selectivity; however, the Cu2+ content has a great influence on the CO2 adsorption properties and catalytic activity of LDHs, which is ascribed to the distortion induced by the Jahn–Teller effect of Cu2+ [46,47,48]. Hence, the preparation of Cu-Mg-Al LDHs with excellent CO2 adsorption performance is of great significance. In this regard, the aims of this work were to prepare, characterize and evaluate the CO2 adsorption capacity and photocatalytic conversion performance of Cu-Mg-Al LDHs with an appropriate Cu2+ content. The as-synthesized materials were prepared by an amine-modified method, while N-aminoethyl-γ-aminopropyltrimethoxysilane as a grafting agent was then characterized to examine its structures and morphologies. The study focused on the effects of the amine-modified method and the Cu2+ content on the CO2 adsorption performance and the kinetics of the adsorption on Cu-Mg-Al LDHs. Substituting part of Mg2+ with Cu2+ during the preparation of LDHs made it possible to improve the CO2 photocatalytic conversion performance.

2. Materials and Methods

2.1. Materials

All of the chemicals were analytical-grade reagents and used as received without any further purification. Copper nitrate trihydrate (Cu(NO3)2·3H2O; ≥98%), magnesium nitrate hexahydrate (Mg(NO3)2·6H2O; ≥98%), aluminum nitrate nonahydrate (Al(NO3)3·9H2O; ≥98%), sodium dodecyl sulfonate (C12H25SO3Na; ≥97%), and N-aminoethyl-γ-aminopropyltrimethoxysilane (C8H22N2O3Si; ≥95%) were purchased from Aladdin Industrial Inc. (Shanghai, China). Sodium hydroxide (NaOH; ≥98%) and toluene (C7H8; ≥99.5%) were obtained from Xilong Scientific Co., Ltd. (Guangzhou, China). Ethanol (C2H5OH; ≥99.7%) was supplied from Anhui Ante Food Co., Ltd. (Suzhou, Anhui, China). Additionally, deionized water was used to formulate the solution throughout the experiment.

2.2. Preparation of Amine-Modified Cu-Mg-Al LDHs

Cu-Mg-Al LDHs materials with a constant MII/MIII mole ratio of 3 were prepared by an amine-modified method while using Cu(NO3)2·3H2O, Mg(NO3)2·6H2O, and Al(NO3)3·9H2O as precursors.
The first-stage process was to synthesize the primary amine-modified LDHs by co-precipitation. About 1.95 g of Al(NO3)3·9H2O, a certain amount of Cu(NO3)2·3H2O, and Mg(NO3)2·6H2O with a Al3+/Cu2+/Mg2+ molar ratio of 1:x:3−x were dissolved in 50 mL deionized water (solution A). Then, 2.83 g of sodium dodecyl sulfonate (DS) and 6.94 g of N-aminoethyl-γ-aminopropyltrimethoxysilane (N) were dissolved in a mixture of 100 mL deionized water and 50 mL ethanol (solution B). The MII:MIII:DS:N substrate mole ratio was 3:1:2:6. Solution A was then added dropwise to solution B at 70 °C. The mixture was stirred, before the pH value was stabilized at 10 ± 0.1 by adding a 1.0 M NaOH solution. After adding solution A, the mixture was then aged for another 4 h with the stirring and temperature maintained. The precipitated solids were isolated by filtration, washed with deionized water and dried under vacuum overnight. Varying the Cu2+ content, three samples were produced with the Al3+:Cu2+:Mg2+ molar ratios of 1:0.75:2.25, 1:1:2, and 1:1.25:1.75. The corresponding samples were labeled as 0.75Cu-Mg-Al DS/N, Cu-Mg-Al DS/N, and 1.25Cu-Mg-Al DS/N. xCu-Mg-Al DS/N was used as a general designation for all three primary amine-modified LDHs. In addition, non-modified, pure Cu-Mg-Al LDHs was named Cu-Mg-Al DS.
The second stage process was to remodify xCu-Mg-Al DS/N by ultrasonic spalling. The dispersion of 1.0 g of xCu-Mg-Al DS/N in 100 mL toluene was subjected to sonication for 5 h with an ultrasonic machine (JY 92-IIN, SCIENTZ, Ningbo, China). The mixture was stirred at 70 °C for 20 h after adding 4 g of N-aminoethyl-γ-aminopropyltrimethoxysilane. The obtained materials were filtered, washed with deionized water and dried under vacuum overnight. The corresponding samples after ultrasonic spalling were labeled as 0.75Cu-Mg-Al N, Cu-Mg-Al N, and 1.25Cu-Mg-Al N. xCu-Mg-Al N was used as a general designation for all three amine-modified LDHs.

2.3. Characterization

The quantitative analyses of carbon, hydrogen, nitrogen, and sulfur contents in the LDHs were performed by an elemental analyzer (VATIO MACRO CUBE; Elementar, Langenselbold, Germany). The structures and compositions of the LDHs were identified by X-ray powder diffraction spectrometer (X’Pert Pro; PNAlytical, Almelo, The Netherlands) with Cu Kα radiation (λ = 0.1541 nm) at 40 kV and 40 mA. The patterns were collected with diffraction angels (2θ) ranging from 2° to 65°. The surface morphologies of the LDHs were observed by a scanning electron microscope (VEGA3; Tescan, Brno, Czech Republic) with an applied voltage of 10 kV. The surface functional groups of the LDHs, under vacuum and dried at 70 °C for 4 h prior to analysis, were detected on a Fourier-transform infrared spectrometer (TENSOR II; Bruker, Karlsruhe, Germany) in a wavelength region of 4000 to 400 cm−1 and in the transmission mode with a resolution of 4 cm−1 for 64 scans. The thermal decompositions of the LDHs were evaluated by a thermogravimetric (TG) analyzer (TG209F3; Netzsch, Luxemburg, Germany) with a N2 flow of 30 mL·min−1 at a heating rate of 10 °C·min−1. The surface elemental compositions of the LDHs were detected by an X-ray photoelectron spectrometer (ESCALAB 250Xi, Thermo Fischer, Waltham, MA, USA) using monochromatic Al Kα as the X-ray source (1486.6 eV). The binding energy was calibrated by using the C 1s peak at 284.6 eV as a reference.

2.4. CO2 Adsorption Capacity and Sequential Adsorption-Regeneration Cycles

The CO2 adsorptions of the amine-modified Cu-Mg-Al LDHs were tested using the TGA method [29]. In a typical test, approximately 10 mg of each sample were loaded into a ceramic microbalance and then pretreated from room temperature to 140 °C at a heating rate of 15 °C·min−1 in a flow of N2 for 30 min to remove any remaining CO2 from synthesis and storage in atmosphere. The temperature was then brought back to the desired adsorption temperature at a cooling rate of 10 °C·min−1 for 30 min. After the sample weight became stable, the gas input was switched from N2 to pure CO2 and then held isothermally for 180 min until the dynamic adsorption equilibrium. The CO2 adsorption capacity was computed according to the mass variation of the sample in the CO2 atmosphere.
In order to evaluate the cyclic adsorption property, the adsorption-regeneration cycle was repeated three times as follows: after pretreatment, the CO2 adsorption was carried out at 30 °C in a pure CO2 atmosphere for 150 min, and regeneration was carried out at 140 °C in the pure N2 atmosphere for 30 min.

2.5. Photocatalytic CO2 Reduction Test

The photocatalytic performance of the sample was carried out in a 500 mL cylindrical airtight reactor (CEL-HXF300, Au-light, Beijing, China) with a 2 cm thick high-transmitting quartz glass on the top. One gram of the sample was spread evenly onto the bottom of the reactor. CO2 was blown into the reactor to ensure pressure stability at 0.1 MPa, and then, the hydrogen pressure was stable at 0.4 MPa. The reactor was illuminated for 1 h by a PerkinElmer 300 W Xe lamp as a simulated light source. After the reaction was over, 30 mL of the gas mixture extracted from the reactor by a syringe were analyzed by a gas chromatograph (GC, GC9790, Fuli, Taizhou, China) equipped with a flame ionization detector (FID) and Porapak Q as the column chromatograph.

3. Results and Discussion

3.1. Characterization Results of Cu-Mg-Al LDHs

3.1.1. Elemental Analysis

The formula for the intercalated molecules was calculated based on the weight percentages of the carbon, hydrogen, nitrogen, and sulfur in the Cu-Mg-Al LDHs, and the amount of the amine loading was calculated as (weight of N content × 1000)/14, as shown in Table 1. Compared with xCu-Mg-Al DS/N, a decrease in the S content of xCu-Mg-Al N indicated that the amine-modified method can exfoliate the intercalated anionic surfactant during ultrasonic spalling. Observed from the formula for intercalated molecules, the increment of amino silanes was greater than the decrement of the anionic surfactant, which indicated that amino silanes partially replaced the anionic active sites and condensed with the surface hydroxyl groups on the laminates.
The amine loading of xCu-Mg-Al N after amine modification was increased significantly, and the more Cu2+ content in the sample, the greater the increase. As Cu2+ continuously replaces Mg2+ in the layer, the charge density of the laminates decreased, which can be attributed to the fact that the charge population of copper was smaller than that of magnesium [49]. Simultaneously, the electrostatic interactions between the cations of laminates and the interlayer anions weakened. Consequently, resulting in the interlayer spacing being expanded implied more conducive to the intercalation of the grafted amino silanes.

3.1.2. XRD Analysis

Figure 1 shows the XRD patterns of xCu-Mg-Al DS/N and xCu-Mg-Al N. In all samples, the nonbasal reflections (006) at a 2θ of about 5° and (110) at a 2θ of about 60° were preserved, indicating that the structure of layers was conserved [29,50]. xCu-Mg-Al DS/N and xCu-Mg-Al N exhibited similar patterns from a rough look. However, each sample had a different intensity of the reflections at the peaks from a careful observation.
According to the Bragg’s Law (2dsinθ = nλ, where θ is the diffraction half-angle and n is the diffraction order) and subtracting the average thickness of the laminate by 0.49 nm [50], the interlayer spacing of Cu-Mg-Al N was calculated to be 3.58 nm by the (003) diffraction peak located at 2.17°. Compared with 1.98 nm of the non-modified Cu-Mg-Al DS and 3.09 nm of the primary amine-modified Cu-Mg-Al DS/N, the enlarged interlayer spacing governed by the size of the anions showed that the amine-modified method can further improve amino silanes grafting.
The intensity and sharpness of the (003) peak reduced gradually with the progress of amine modification and the increase of the Cu2+ content, and the overlapping of the peaks corresponding to the (015) and (018) reflections occurred. Combined with the amine loading data of the elemental analysis in Table 1, it was shown that the crystallinity of the particles decreased after augmenting amino silanes grafting sites [50].
It is noticeable that as the Cu2+ content increased, the (003) peak of 1.25Cu-Mg-Al N detectably shifted toward a large angle, and the reflection in the 2θ range of 15° to 30° became narrow, which is mainly due to the distortion induced by the Jahn–Teller effect of Cu2+. With an increase of the Cu2+ content in the layer, this distortion weakened the hydrogen bonding and the electrostatic interactions between the host layer and the guest. The absolute value of the binding decreased, and the chemical stability of the system decreased as well. Correspondingly, the interlayer spacing of 1.25Cu-Mg-Al N was shortened to 3.17 nm, which displayed that the host layer and the guest needed to be close to each other in order to increase the interaction force [51] and how seriously the stability of the system declined.

3.1.3. Microstructure Observation

The morphologies of xCu-Mg-Al N and xCu-Mg-Al DS/N were further confirmed by SEM micrographs. The particle size and the surface morphology of xCu-Mg-Al N (Figure 2a–c) changed dramatically by the amine-modified method when compared to those of xCu-Mg-Al DS/N (Figure 2d–f). The surface of xCu-Mg-Al DS/N had a plate-like shape. The diameters of xCu-Mg-Al N ranged from 20 to 50 μm, which were averagely smaller than the lateral sizes of xCu-Mg-Al DS/N, accompanied by a completely loading with small particles on the surface.
The Cu2+ content also had a greater influence on the surface morphology of xCu-Mg-Al N. Compared with the chunky grafts aggregated on the surface of 0.75Cu-Mg-Al N (Figure 2a), dispersing Cu-Mg-Al N (Figure 2b) into granular grafts was more favorable for CO2 trapping and adsorption to some extent. The surface of 1.25Cu-Mg-Al N (Figure 2c) was abnormally smooth with remarkably increased agglomeration, which speculated that the surface grafts were polymerized to maintain the system stability. The high Cu2+ content introduced more defects into the system and resulted in excessive distortion by the Jahn–teller effect, which was consistent with the XRD pattern results and supported our inference.

3.1.4. FTIR Analysis

FTIR analysis was further conducted to identify functional groups on the surface of LDHs. Figure 3 shows the variations in the FTIR spectra of xCu-Mg-Al DS/N and xCu-Mg-Al N. For xCu-Mg-Al DS/N, the bands at 3250 cm−1 (stretching vibration of –NH2 groups) and 1588 cm−1 (bending vibration of –NH2 groups) were assigned to the characteristic absorption bands of amino silanes; meanwhile, apparent peaks at 1185/1140 cm−1 (stretching vibration of –SO3) were observed, corroborating that N-aminoethyl-γ-aminopropyltrimethoxysilane and sodium dodecyl sulfonate were grafted to the LDH layer in the form of salt after the primary amine modification.
For xCu-Mg-Al N, a further improvement of amino silanes grafting after amine modification was confirmed by the presence of new peaks at 1311 cm−1 for the stretching vibration of N–C and 1114 cm−1 for the stretching vibration of Si–O–C. The weakening of the –SO3 stretching vibration after amine modification may be due to the exfoliation of LDH laminates by ultrasonication. The intensities of those characteristic bands were substantially enhanced by felicitously increasing the Cu2+ content. In other words, the surface functional groups of Cu-Mg-Al N were similar to those of 0.75Cu-Mg-Al N, but the surface grafts of Cu-Mg-Al N were denser. Previous predictions are consistent with the results of the microstructure observation and the elemental analysis.
For 1.25Cu-Mg-Al N, the intensities of the –OH stretching vibration in the range of 3300 to 3500 cm−1 were significantly weaker than those of 0.75Cu-Mg-Al N and Cu-Mg-Al N, indicating that the amine loading of 1.25Cu-Mg-Al N was increased obviously. What’s more, the bending vibration of –NH2 groups at 1588 cm−1 overlapped with the stretching vibration of water molecules in the same IR region of 1.25Cu-Mg-Al N, which may be due to the fact that amino silanes polymerized on the surface and the content of the free-amino groups was greatly reduced.

3.1.5. Thermal Analysis

TG study was carried out to investigate the thermal stability of the samples. As it is presented in Figure 4, the Cu-Mg-Al LDHs underwent three stages of mass loss. The first stage occurring below 150 °C may be attributed to the removal of the interlayer water and the physically adsorbed CO2 [28]; the second stage appearing in the range from 150 to 300 °C mainly may be ascribed to substrate dehydroxylation [52]; the third stage detected at temperatures over 300 °C may be assigned to the carbon chain decomposition of anionic surfactants and amino silanes [29].
As seen from Table 2, the weight loss ratio of xCu-Mg-Al N in the second stage was obviously lower than that of xCu-Mg-Al DS/N, which indicated that the free-hydroxyl groups on the surface of the material decreased after being remodified by ultrasonic spalling. It was inferred that the amine-modified process with more grafted amino silanes can promote the condensation between the amino silanes and the surface hydroxyls on the laminates. The weight loss ratios in the third stage were significantly different. The weight loss ratios of 0.75Cu-Mg-Al N and Cu-Mg-Al N were lower than those of the corresponding primary amine-modified LDHs, while the weight loss ratio of 1.25Cu-Mg-Al N was higher than that of the corresponding primary amine-modified LDH. Combined with the formula for the intercalated molecules in Table 1, the former was attributed to the fact that the increase of the amine loading was similar to that of the anionic surfactant removal and the molecular weight of the amino silane was obviously smaller than that of the anionic surfactant, while the latter can be related to the fact that the increment of the amino silanes was much greater than the decrement of the anionic surfactant.
It was noted that the weight loss ratios of xCu-Mg-Al N decreased in the first two stages accompanied by the Cu2+ content increase. Associated with the formula for the intercalated molecules in Table 1, the first stage may be interpreted that the interlayer anionic sites were gradually replaced by amino silanes, of which the hydrophilicity was weaker than that of the anionic surfactants. The second stage may be due to the consumption of the free-hydroxyl groups promoted by Cu2+. Furthermore, one obvious difference is that the weight loss ratio of 1.25Cu-Mg-Al N increased on the third stage, and it was speculated that part of amino silanes on the surface of sample may have been polymerized.

3.1.6. XPS Analysis

The effect of the Cu2+ content on the aminated functional groups in the amine modification process was further investigated via XPS analysis. N 1s spectra were recorded in Figure 5 to analyze the surface compositions of the samples. The high-resolution N 1s spectra of xCu-Mg-Al N (Figure 5a–c) can be deconvoluted into two peaks at ca. 399.3 eV (peak 1) and 401.3 eV (peak 2) binding energies, which corresponded to free amine and protonated amines, respectively [53], and that of xCu-Mg-Al DS/N (Figure 5d–f) was slightly offset. As seen from Figure 5, the contents of the free amines and protonated amines on the surface of xCu-Mg-Al N were more than those of xCu-Mg-Al DS/N, which indicated that increasing the surfactant removal rate significantly improved the amine loading on the surface of the samples. As the addition of Cu2+ increased, a higher concentration of free amines was shown, which revealed that there were comprehensive amino group active sites readily available for CO2 adsorption.
The XPS spectra of the Cu 2p region were utilized to better verify the chemical states of Cu species in the samples, as shown in Figure 6. Two main peaks were observed at binding energies of ca. 952 and 932 eV. In a nutshell, the peak at the binding energy of ca. 932 eV can be deconvoluted into two sets of peaks, in which the peaks at ca. 934.3 eV (peak 3) and 932.3 eV (peak 1) can be assigned to 2p3/2 of Cu2+ and 2p3/2 of either Cu0 and/or Cu+, respectively [54]. The former peak can be assigned to Cu2+ species, and the latter may be related to another state where Cu ions coordinate with Mg and Al ions in a spinel-like species [55]. The other two peaks at ca. 954.4 eV (peak 4) and 952.1 eV (peak 2) deconvoluted by the peak at the binding energy of ca. 952 eV can correspond to 2p1/2 of Cu2+ and 2p1/2 of either Cu0 and/or Cu+, respectively. Unlike the others, the area of peak 4 for 1.25Cu-Mg-Al N was obviously higher than those of the others, even 0 for Cu-Mg-Al N, which revealed that the disappearance of 2p1/2 of Cu2+ at the high energy side was better in promoting CO2 adsorption.

3.2. CO2 Adsorption Performance

3.2.1. Effect of the Amine Loading

The amine loading through the availability of basic amine groups mainly determines the CO2 adsorbents of solid-supported amine materials [28,56]. Figure 7 displays the relationship between the CO2 adsorption capacity of the samples and the amine loading according to elemental analysis at 30 °C and a 0.1 MPa pure CO2 atmosphere. As the Cu2+ content increased, the total amine loading of each sample increased, whereas the correlation of CO2 adsorption capacity with the Cu2+ content increase was not positive. The CO2 adsorption capacities of 0.75Cu-Mg-Al N and Cu-Mg-Al N both increased by over 1 mmol·g−1 when compared to those of the corresponding primary amine-modified LDHs, indicating that the amine-modified method can significantly improve the CO2 adsorption performance of the material. In contrast, 1.25Cu-Mg-Al N exhibited a very disheartening CO2 adsorption capacity down to 0.70 mmol·g−1, which was even lower than that of 1.25Cu-Mg-Al DS/N. It suggested that the amine loading was not the only factor affecting the CO2 adsorption performance of the material [52]. The phenomenon of the inhibited CO2 adsorption can be explained by the increase in the interlayer spacing, caused by the decrease in the charge density of the laminates due to overdoped Cu2+, promoting the intercalation of amino silanes and weakening the stability of the materials; meanwhile, the distortion induced by the Jahn–Teller effect led to the mass polymerization of amino silanes on the sample surface.

3.2.2. Effect of the Temperature

Figure 8 shows the CO2 adsorption capacities of xCu-Mg-Al N and xCu-Mg-Al DS/N at three different temperatures at a 0.1 MPa pure CO2 atmosphere. The CO2 adsorption capacities of all samples decreased with the increasing temperature, and the highest one was up to 1.82 mmol·g−1 for Cu-Mg-Al N at 30 °C. This is due to the reaction being exothermic and the increase in the temperature being unfavorable to the adsorption. Nevertheless, the adsorption capacities of 0.75Cu-Mg-Al N and Cu-Mg-Al N at higher temperatures in the range of 1.4 to 1.7 mmol·g−1 were much larger than those of the primary amine-modified samples, which suggested that Cu-Mg-Al LDHs prepared by the amine-modified method have the potential to be used in the adsorption of flue gas from fossil fuel-based thermal power plants. Simultaneous with the temperature of the reactor rising during the photocatalysis process, this conclusion provides the theoretical support of adsorption for further applications of Cu-Mg-Al LDHs to the CO2 photocatalytic conversion.
For a comparison, the CO2 adsorption capacities for the amine-modified LDHs, as reported in the literature, are listed in Table 3, where it can be seen that the CO2 adsorption capacity of Cu-Mg-Al N was either better or comparable with those of many other materials investigated.

3.2.3. Effect of Sequential Adsorption-Regeneration Cycles

The stable recycling performance of adsorbents is a key research content in industrial process. Figure 9 represents the cyclic adsorption-regeneration performance of Cu-Mg-Al N, which showed a better adsorption property in previous experiments. The deactivation rate of the adsorbent was calculated by dividing the difference in the adsorption capacities between the 1st and 2nd cycles by adsorption capacity after the 1st cycle. The Cu-Mg-Al N adsorbent exhibited a slight decrease in the deactivation rate of only 8% from the initial stage to the 3rd cycle, which may be attributed to the formation of stable semicarbazide deposited on the adsorbent by the dehydration of a small fraction of CO2 with the amino group at high temperatures [53,57]. This result revealed that Cu-Mg-Al N displayed excellent adsorption performance stability throughout three sequential adsorption-regeneration cycles, which is also an essential criterion for practical applications.

3.2.4. Adsorption Kinetics

Adsorption kinetics analysis is an important index to evaluate the efficiency of adsorbents [58]. Pseudo-first-order, pseudo-second-order, and double-exponential models were applied to the experimental data on Cu-Mg-Al LDHs through nonlinear regression. The kinetic parameters are presented in Table 4, and the fitting curves under different kinetic models were compared with the experimental data points in Figure 10. From the comparison results, it can be seen that double-exponential model displayed a comparatively good fit with the CO2 adsorption process of Cu-Mg-Al LDHs.
Loganathan et al. [59] found that the excellent fit obtained using the double-exponential model resulted from its capacity to account for both the physical and chemical adsorptions of CO2 on an adsorbent. The factors A1 and A2 of the double-exponential model in Table 4 represent the maximum adsorption capacity, while k1 and k2 stand for the kinetic rate constants of the two adsorption sites. The lower value of k1 corresponds to the physisorption site through intra-particle diffusion, whereas the higher value of k2 accounts for the chemisorption site through strong surface reactions. From the A1 and A2 values of xCu-Mg-Al N and xCu-Mg-Al DS/N, it can infer that CO2 adsorption takes place via chemisorptive and physisorptive interactions. The remarkable improvements in the overall adsorption performances of 0.75Cu-Mg-Al N and Cu-Mg-Al N were assigned to the obvious enhancements in both physisorption and chemisorption after amine modification. The suppressed chemisorption of 1.25Cu-Mg-Al N caused by the agglomeration of particles was predominant in the unimproved adsorption performance, although physisorption was enhanced.

3.3. Photocatalytic CO2 Reduction

The influences of different photocatalysts on the catalytic activity were investigated by CO2 reduction under a solar simulator, and the relevant parameters of gas chromatography analysis are shown in Table 5. Compared with Mg-Al N without the Cu2+ doping, methanol could be obtained by the CO2 reduction with both Cu-Mg-Al DS/N and Cu-Mg-Al N as photocatalysts, which indicated that Cu2+ was the active site of photocatalytic reaction, and demonstrated the potential of amine-modified Cu-Mg-Al LDHs in the field of photocatalytic reduction to methanol.
The methanol yield of Cu-Mg-Al N was significantly higher than that of Cu-Mg-Al DS/N, that is, more photocatalytic active sites provided by Cu-Mg-Al N, which resulted in the higher photocatalytic conversion efficiency of Cu-Mg-Al N [60]. It suggested that amine modification not only conspicuously improves the CO2 adsorption capacity, but also the CO2 photocatalytic conversion performance, which may be due to the coupling effect between them. In other words, the CO2 consumption by the reduction reaction promoted the adsorption equilibrium to move forward. Simultaneously, the strong adsorption increased the concentration of CO2 on the material surface, especially on the active site of Cu2+, thus promoting the catalytic reduction reaction.

4. Conclusions

Amine-modified photocatalysts Cu-Mg-Al LDHs have been prepared using N-aminoethyl-γ-aminopropyltrimethoxysilane as a grafting agent. The CO2 adsorption capacity of Cu-Mg-Al N was up to 1.82 mmol·g−1 at 30 °C and a 0.1 MPa pure CO2 atmosphere. The amine-modified method and an appropriate Cu2+ content have great influences on the surface morphology of the materials, and promising amine loadings and the surface free-amino functional groups were obtained. The kinetic model confirmed that the complex CO2 adsorption mechanism of Cu-Mg-Al LDHs involves a rapid phase controlled by chemical adsorption with strong surface reactions and a slow phase controlled by physical adsorption with intraparticle diffusion. Both of them were enhanced with the increase of the Cu2+ content, while chemical adsorption was suppressed when the Cu2+ content was too high. A slight decrease in the adsorption capacity at high temperatures and excellent adsorption performance stability throughout three sequential adsorption-regeneration cycles of Cu-Mg-Al N provided theoretical supports of adsorption for its further application to CO2 photocatalytic conversion. Cu-Mg-Al N can photocatalytically reduce CO2 to methanol with Cu2+ as an active site, which fully demonstrated its potential in the fields of photocatalysis and adsorption of flue gas from power plants.

Author Contributions

Conceptualization, N.A.; formal analysis, Q.W., Q.Y. and Y.Z.; funding acquisition, N.A.; investigation, Q.W. and Y.Z.; project administration, N.A.; writing—original draft, Q.W., Q.Y. and Y.Z.; writing—review and editing, Q.W. and J.R. All authors have read and agreed to the published version of the manuscript.

Funding

This research was supported by the Open Project Program of the State Key Laboratory of Chemical Engineering (SKL-ChE-11A02), Zhejiang Provincial Natural Science Foundation of China (grant No. LY16B060014) and lateral project of Zhejiang University of Technology (HG-[2016]051@).

Institutional Review Board Statement

Not applicable.

Informed Consent Statement

Not applicable.

Data Availability Statement

The data presented in this study are available from the corresponding author on request.

Conflicts of Interest

The authors declare no conflict of interest.

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Figure 1. XRD diffraction patterns of Cu-Mg-Al DS, xCu-Mg-Al DS/N, and xCu-Mg-Al N at different 2θ ranges: (a) 2θ range of 2°–10°; (b) 2θ range of 10°–65°.
Figure 1. XRD diffraction patterns of Cu-Mg-Al DS, xCu-Mg-Al DS/N, and xCu-Mg-Al N at different 2θ ranges: (a) 2θ range of 2°–10°; (b) 2θ range of 10°–65°.
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Figure 2. SEM micrographs of the samples: (a) 0.75Cu-Mg-Al N; (b) Cu-Mg-Al N; (c) 1.25Cu-Mg-Al N; (d) 0.75Cu-Mg-Al DS/N; (e) Cu-Mg-Al DS/N; (f) 1.25Cu-Mg-Al DS/N.
Figure 2. SEM micrographs of the samples: (a) 0.75Cu-Mg-Al N; (b) Cu-Mg-Al N; (c) 1.25Cu-Mg-Al N; (d) 0.75Cu-Mg-Al DS/N; (e) Cu-Mg-Al DS/N; (f) 1.25Cu-Mg-Al DS/N.
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Figure 3. FTIR spectra of the samples: (a) xCu-Mg-Al DS/N; (b) xCu-Mg-Al N.
Figure 3. FTIR spectra of the samples: (a) xCu-Mg-Al DS/N; (b) xCu-Mg-Al N.
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Figure 4. Thermogravimetric (TG) curves of the samples: (a) xCu-Mg-Al DS/N; (b) xCu-Mg-Al N.
Figure 4. Thermogravimetric (TG) curves of the samples: (a) xCu-Mg-Al DS/N; (b) xCu-Mg-Al N.
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Figure 5. The high-resolution spectra of N 1s of xCu-Mg-Al DS/N and xCu-Mg-Al N: (a) 0.75Cu-Mg-Al N; (b) Cu-Mg-Al N; (c) 1.25Cu-Mg-Al N; (d) 0.75Cu-Mg-Al DS/N; (e) Cu-Mg-Al DS/N; (f) 1.25Cu-Mg-Al DS/N.
Figure 5. The high-resolution spectra of N 1s of xCu-Mg-Al DS/N and xCu-Mg-Al N: (a) 0.75Cu-Mg-Al N; (b) Cu-Mg-Al N; (c) 1.25Cu-Mg-Al N; (d) 0.75Cu-Mg-Al DS/N; (e) Cu-Mg-Al DS/N; (f) 1.25Cu-Mg-Al DS/N.
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Figure 6. The high-resolution spectra of Cu 2p of xCu-Mg-Al DS/N and xCu-Mg-Al N: (a) 0.75Cu-Mg-Al N; (b) Cu-Mg-Al N; (c) 1.25Cu-Mg-Al N; (d) 0.75Cu-Mg-Al DS/N; (e) Cu-Mg-Al DS/N; (f) 1.25Cu-Mg-Al DS/N.
Figure 6. The high-resolution spectra of Cu 2p of xCu-Mg-Al DS/N and xCu-Mg-Al N: (a) 0.75Cu-Mg-Al N; (b) Cu-Mg-Al N; (c) 1.25Cu-Mg-Al N; (d) 0.75Cu-Mg-Al DS/N; (e) Cu-Mg-Al DS/N; (f) 1.25Cu-Mg-Al DS/N.
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Figure 7. Relationships between the CO2 adsorption capacity and the amine loading content for xCu-Mg-Al DS/N and xCu-Mg-Al N.
Figure 7. Relationships between the CO2 adsorption capacity and the amine loading content for xCu-Mg-Al DS/N and xCu-Mg-Al N.
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Figure 8. CO2 adsorption capacities of xCu-Mg-Al N and xCu-Mg-Al DS/N with different temperatures.
Figure 8. CO2 adsorption capacities of xCu-Mg-Al N and xCu-Mg-Al DS/N with different temperatures.
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Figure 9. Adsorption-regeneration cycling results of Cu-Mg-Al N.
Figure 9. Adsorption-regeneration cycling results of Cu-Mg-Al N.
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Figure 10. Comparison of different kinetic models with the experimental data of the CO2 adsorption on 0.75Cu-Mg-Al DS/N (a), 0.75Cu-Mg-Al N (b), Cu-Mg-Al DS/N (c), Cu-Mg-Al N (d), 1.25Cu-Mg-Al DS/N (e), and 1.25Cu-Mg-Al N (f).
Figure 10. Comparison of different kinetic models with the experimental data of the CO2 adsorption on 0.75Cu-Mg-Al DS/N (a), 0.75Cu-Mg-Al N (b), Cu-Mg-Al DS/N (c), Cu-Mg-Al N (d), 1.25Cu-Mg-Al DS/N (e), and 1.25Cu-Mg-Al N (f).
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Table
Table 1. Elemental analysis results of xCu-Mg-Al DS/N and xCu-Mg-Al N.
Table 1. Elemental analysis results of xCu-Mg-Al DS/N and xCu-Mg-Al N.
SampleElemental Weight (%)Formula for Intercalated MoleculesAmine Loading
NCHS(mmol·g−1)(mmol·g−1)
0.75Cu-Mg-Al DS/N6.3136.587.653.95(C12H25SO3−)1.24(C6.95H20.23SiN2O3)2.254.51
Cu-Mg-Al DS/N6.5736.627.714.47(C12H25SO3−)1.40(C5.87H17.96SiN2O3)2.354.69
1.25Cu-Mg-Al DS/N7.1536.277.534.28(C12H25SO3−)1.34(C5.55H16.39SiN2O3)2.555.11
0.75Cu-Mg-Al N8.2934.347.422.04(C12H25SO3−)0.64(C7.08H19.68SiN2O3)2.965.92
Cu-Mg-Al N9.7036.307.491.49(C12H25SO3−)0.47(C7.12H18.26SiN2O3)3.466.93
1.25Cu-Mg-Al N11.7535.987.831.46(C12H25SO3−)0.46(C5.84H15.94SiN2O3)4.208.39
Table
Table 2. Weight loss ratios of xCu-Mg-Al DS/N and xCu-Mg-Al N.
Table 2. Weight loss ratios of xCu-Mg-Al DS/N and xCu-Mg-Al N.
SampleFirst Stage (%)Second Stage (%)Third Stage (%)
0.75Cu-Mg-Al DS/N7.78.543.2
Cu-Mg-Al DS/N6.19.747.8
1.25Cu-Mg-Al DS/N4.810.139.9
0.75Cu-Mg-Al N13.56.539.7
Cu-Mg-Al N10.56.337.0
1.25Cu-Mg-Al N8.96.142.4
Table
Table 3. CO2 adsorption capacities for the amine-modified layered double hydroxides (LDHs), as cited in the literature.
Table 3. CO2 adsorption capacities for the amine-modified layered double hydroxides (LDHs), as cited in the literature.
SampleGrafting AgentTemperature (°C)CO2 Adsorption (Capacity mmol−1·g−1)Reference
Mg-Al N2N-aminoethyl-γ-aminopropyltrimethoxysilane302.26[26]
NiMgAl N2N-[3-(Trimethoxysilyl)propyl]ethylenediamine802.02[27]
Cu-Mg-Al NN-aminoethyl-γ-aminopropyltrimethoxysilane301.82This work
MgAl N3 3-[2-(2-Aminoethylamino) ethylamino]propyl-trimethoxysilane801.76[28]
UL30-LDHN-aminoethyl-gamma-aminopropyltrimethoxysilane301.65[56]
MgAl MEA 13-aminopropyl triethoxysilane251.39[29]
UH-MEA5(3-aminopropyl)-triethoxysilane551.37[57]
N1-HMS@Mg-Al LDHN1-(3-Trimethoxysilylpropyl) diethylenetriamine751.28[23]
Table
Table 4. Parameters of CO2 kinetic models, R2, and standard errors (%) for xCu-Mg-Al N and xCu-Mg-Al DS/N at 30 °C and 1 atm.
Table 4. Parameters of CO2 kinetic models, R2, and standard errors (%) for xCu-Mg-Al N and xCu-Mg-Al DS/N at 30 °C and 1 atm.
SamplesPseudo-1st-OrderErrR2Pseudo-2nd-OrderErrR2Double-ExponentialErrR2
qekf(%) qekf(%) qeA1A2k1k2(%)
0.75Cu-Mg-Al DS/N0.610.060.450.81390.670.130.430.93720.700.350.360.010.310.180.9989
Cu-Mg-Al DS/N0.720.020.560.93570.860.030.710.97180.800.590.220.010.370.180.9993
1.25Cu-Mg-Al DS/N0.690.030.620.86750.800.060.740.94380.880.550.310.010.200.420.9994
0.75Cu-Mg-Al N1.690.041.310.84091.890.031.350.94341.971.070.940.010.270.720.9987
Cu-Mg-Al N1.670.071.110.82701.830.050.970.94971.920.861.110.010.260.680.9983
1.25Cu-Mg-Al N0.730.010.820.97720.990.011.250.98661.010.860.150.010.120.620.9999
Table
Table 5. Product chromatographic results for different photocatalysts.
Table 5. Product chromatographic results for different photocatalysts.
CatalystProductRetention Time (min)Content (%)
Mg-Al NCO20.4734.30
H20.97395.40
Cu-Mg-Al DS/NCO20.5203.76
H21.02083.08
CH3OH3.85012.40
Cu-Mg-Al NCO20.5303.43
H21.03077.24
CH3OH3.84018.53
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Wang, Q.; Yan, Q.; Zhao, Y.; Ren, J.; Ai, N. Preparation of Amine-Modified Cu-Mg-Al LDH Composite Photocatalyst. Nanomaterials 2022, 12, 127. https://doi.org/10.3390/nano12010127

AMA Style

Wang Q, Yan Q, Zhao Y, Ren J, Ai N. Preparation of Amine-Modified Cu-Mg-Al LDH Composite Photocatalyst. Nanomaterials. 2022; 12(1):127. https://doi.org/10.3390/nano12010127

Chicago/Turabian Style

Wang, Qining, Quanwang Yan, Yu Zhao, Jie Ren, and Ning Ai. 2022. "Preparation of Amine-Modified Cu-Mg-Al LDH Composite Photocatalyst" Nanomaterials 12, no. 1: 127. https://doi.org/10.3390/nano12010127

APA Style

Wang, Q., Yan, Q., Zhao, Y., Ren, J., & Ai, N. (2022). Preparation of Amine-Modified Cu-Mg-Al LDH Composite Photocatalyst. Nanomaterials, 12(1), 127. https://doi.org/10.3390/nano12010127

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