Dysprosium Oxide-Supported CaO for Thermochemical Energy Storage

Abstract

A novel CaO-based material supported with Ca₃Al₂O₆ and Dy₂O₃ was found to show excellent performance as a thermochemical energy storage material for use in solar thermal power plants. It retains a carbonation conversion capacity of 82.7% for a period of 40 cycles, as well as exothermic heats of reaction of 582.2 kJ kg⁻¹, up to seven times greater than other materials found in the literature. The improved performance was attributed to the greater prevention of sintering and retention of high surface area by the addition of two inert supports: Ca₃Al₂O₆ and Dy₂O₃. Long-term effectiveness of the novel material was also evaluated by using a sintering model. It retains an energy storage utilization of 6.2 kg kWh⁻¹ after 30 years of cycling, while commercial limestone would require 81 tons kWh⁻¹ equivalent. Limestone requires replacement every six thermal cycles, making it impractical for real thermochemical energy storage implementation. The extra cost associated with the addition of supports in this CaO-based material is justified by the long-term durability, which would imply a reduction in the overall capital and operational expenditure of the plant.

Introduction

Renewable energy generation and storage systems are a key strategy in order to reduce CO₂ emissions and limit global warming (Greenblatt et al., 2017). CO₂ capture technologies are essential for transitioning into novel renewable energy-based society while still obtaining an economic return on the current infrastructure. However, CO₂ capture itself is not enough to solve the emissions problem. CO₂ capture technologies could be coupled with CO₂ storage, which solves in part the problem of taking carbon emissions out of the atmosphere. Thus, if instead of storing CO₂ we can utilize it effectively for other purposes, then there is a benefit (not only cost) on the carbon emissions. Nowadays, CO₂ is widely use in food industry for conservation. However, this CO₂ is not reused it in a way that it is easily storable and utilize.

Commercial concentrated solar power (CSP) plants employ sensible heat storage, and various candidate solar salts and other storage media have been explored (Gil et al., 2010; Liu M. et al., 2016). However, CSP plants require a higher levelized cost of electricity than other renewable alternatives, limiting deployment of these technologies (Starke et al., 2018; Awan et al., 2019). One of the main alternatives for cost reduction is replacing the low- efficiency subcritical Rankine cycle with the highly efficient supercritical CO₂ Brayton power cycle. Specifically, this power cycle has been demonstrated to achieve solar to electricity efficiencies as high as 55% when operating at temperatures around 700°C (Calle et al., 2018). However, there are no commercially established energy storage systems for power cycles operating at such high temperatures. A promising alternative is the use of thermochemical energy storage (TCES) (André et al., 2016; Prieto et al., 2016; André and Abanades, 2018). The gas-solid reactions involved in TCES have high energy storage densities, making the process suitable for long-term energy storage (Bayon et al., 2018). Of all TCES technologies under investigation currently, carbonate looping has been found to have the greatest potential in the range of temperatures suitable for supercritical CO₂ Brayton cycles (Bayon et al., 2018).

The carbonate looping cycle based on CaCO₃ has been well researched for both TCES storage (Chacartegui et al., 2016; Prieto et al., 2016; Benitez-Guerrero et al., 2017, 2018; Ortiz et al., 2018a, b); and CO₂ capture technologies (Grasa et al., 2008; Erans et al., 2018). The calcination reaction is endothermic and can be driven by concentrated solar energy, as shown in Eq. (1), where ΔH_r is the reaction enthalpy (kJ mol^–1). The reaction products, CaO and CO₂, are stored separately. The reverse carbonation reaction recombines the calcination products in a separate reactor, releasing heat to be transferred to the gas turbine (Edwards and Materić, 2012); i.e.,

One of the major challenges associated with carbonate looping is the declining conversion efficiency of the carbonation reaction with ongoing thermal cycling. According to Grasa et al. (2008) carbonation conversion decreases dramatically during the first 20 cycles to a reversible conversion of about 8%. This results in a large proportion of inactive CaO cycling through the carbonate looping system, which leads to increased capital and operating costs (Edwards and Materić, 2012). At high calcination temperatures (>850°C), the decrease in the extent of conversion has been mainly attributed to the sintering of CaO grains (Benitez-Guerrero et al., 2017). The driving force for sintering is the reduction of surface energy of the grains caused by decreasing their surface area or increasing their grain size (Stone, 1960). Reducing the surface area reduces CaO reactivity by decreasing the amount of active sites available for the carbonation reaction (Liu W. et al., 2016), leading to longer CO₂ diffusion pathways.

High sintering resistance is related to the refractory nature of a material. Tammann temperature provides an indication for a material’s susceptibility to sintering (Aihara et al., 2001). The correlation between Tammann (T_T) and melting temperatures (Tm) is described by the following relationship:

Hence, supporting materials with melting points higher than that of CaCO₃ (such as Dy₂O₃) will theoretically impart sintering-resistant properties to the sorbent (Liu et al., 2012b).

The onset of sintering is influenced by other factors in addition to the material’s Tammann temperature, such as particle size and morphology, including the extent of porosity. For a discussion of the role of supports from a morphological perspective, see section “Characterization Results.”

In order to improve carbonation efficiency and hence cyclability, the use of synthetic CaO-based materials synthesized with sintering-resistant inert supports is well documented (for CO₂ capture applications) (Liu et al., 2012b). A variety of materials have been investigated, such as CaTiO₃ (Liu et al., 2012b), Al₂O₃ (Broda et al., 2012), Y₂O₃ (Derevschikov et al., 2011), SiO₂ (Li et al., 2014; Sanchez-Jimenez et al., 2014), and oxides of Si, Co, Ti, Cr, Ce, and Zr (Lu et al., 2009). Synthesis processes usually involve dispersing CaO in a stable, solid matrix made up of the inert material, acting to preserve the available active surface layer of CaO and preventing loss of conversion with cycling (Li et al., 2005). Some of the most extensively investigated supports include aluminium-containing materials such as calcium aluminates, which form different polymorphs depending on the preparation method; e.g., mayenite (Ca₁₂Al₁₄O₃₃) (Li et al., 2005; Liu et al., 2012a), Ca₉Al₆O₁₈ (Zhou et al., 2012, 2013; Radfarnia and Sayari, 2015), or Ca₃Al₂O₆ (Angeli et al., 2014; Li et al., 2015; Sun et al., 2016; Wang et al., 2018). These supports have been found to be highly effective at stabilizing CaO, particularly when Ca₃Al₂O₆ is prepared using nitrate precursors (Zhou et al., 2012; Azimi et al., 2019). There is less research on the use of active supports as dopants for CaO-based sorbents. Active supports which have been examined include MgO (both dolomites and synthetically doped sorbents) (Albrecht et al., 2008; Liu et al., 2012a; Ping et al., 2016) and Li₂SO₄ (Lu and Wu, 2016).

Recently, lanthanides have become an attractive group of materials for use as supports. Several lanthanides have been tested as supports for CaO for CO₂ capture technologies, both active (able to absorb CO₂) (Cotton et al., 1999) and inactive (Luo et al., 2010). A CaO/La₂O₃ material produced using sol-gel combustion synthesis displayed good performance for 20 cycles under both inert gas and 100% CO₂ atmosphere (Luo et al., 2010). A CaO/La₂O₃ composite was also synthesized by Albrecht et al. (2008) using a hydrothermal process with nitrate precursors, limestone and tetrahydrofuran as a solvent. Materials containing small amounts of La₂O₃ showed a higher absorption capacity through 30 cycles than untreated limestone. However, this benefit was not retained with longer term cycling, with CO₂ capture capacity comparable to that of untreated limestone after 80 cycles (Albrecht et al., 2008).

Hu et al. (2015) incorporated Nd₂O₃ into CaO particles by wet mixing for CO₂ capture purposes. Improved durability and higher carbonation conversion were observed (67% after 100 cycles at a calcination temperature of 900°C), which was attributed to the prevention of sintering (Hu et al., 2015). Although the authors describe Nd₂O₃ as an inert solid sorbent, it is actually an effective CO₂ sorbent (Perry, 2015). Taking this into account and noting the drop off in conversion capacity at more severe calcination conditions, it is likely that the improved carbonation conversion is also due to the CO₂ uptake of Nd₂O₃ compared to inactive supports such as calcium aluminate. Hu et al. (2016) also supported CaO with Yb₂O₃, which achieved modest sintering-resistance (17% carbonation conversion after 50 cycles when tested under severe calcination conditions, a 9.5% improvement compared to CaO). However, the use of Pr₆O₁₁ as a support for CaO was unsuccessful, which was attributed to its very high molecular weight (Hu et al., 2016).

To address the challenge of finding a material that exhibits durability with thermal cycling under TCES conditions (high calcination temperature and 100% CO₂ atmosphere), this work proposed the use of Dy₂O₃ as a support to CaO. It is envisaged that the use of Dy₂O₃ will be beneficial due to its high melting temperature (∼2340°C), which predicts high sintering resistance (Liu et al., 2012b). This is supported by the improved performance of lanthanide-supported CaO in the literature (Luo et al., 2010; Hu et al., 2015, 2016).

The inert support mayenite (Ca₁₂Al₁₄O₃₂) has been consistently shown to prevent sintering, despite possessing a comparatively low Tammann temperature (Li et al., 2005; Liu et al., 2012a). This work also proposes a combination of Dy₂O₃ and Ca₃Al₂O₆ which obtains exceptional sintering resistance, improving the durability of CaO as compared with other explored supports with smaller amount of inactive material. A further long-term performance analysis reveals that the use of Dy₂O₃ and Ca₃Al₂O₆ could also be feasible compared with other TCES materials, as no replacement of the storage material is required during the typical lifetime of a CSP plant (commonly 30 years) (Liu M. et al., 2016).

Experimental

Materials Preparation

Pechini-synthesized CaO (denoted as P-CaO or P-CaCO₃ in its carbonate form) was prepared using the Pechini method, following the steps described in the literature (Jana et al., 2010). The reagents utilized were Ca(NO₃)₂ (Sigma-Aldrich; 99.0% purity), Al(NO₃)₃ (Sigma-Aldrich; 99.0% purity), dysprosium(III) nitrate hydrate (Dy(NO₃)₃.xH₂O); (Sigma-Aldrich; 99.9% purity), citric acid (CA; C₆H₈O₇; Sigma-Aldrich; 99.5% purity) and ethylene glycol (EG; HOCH₂CH₂OH; Sigma-Aldrich; 99.8% purity). The quantities of the reagents used are shown in Table 1 as well as the nomenclature of the synthesized products. A precursor with a CA molar ratio of 1:5 and a CA to EG ratio of 3:2 were utilized.

Approximately 0.3 mol (57.4 g) of CA was added to 100 mL of distilled water (Milli-Q) and stirred at 70°C until dissolved totally. The metal precursors Ca(NO₃)₂ (11.8 g) and Dy(NO₃)₃ (1.3 g) were then added to the solution, which was stirred for 3 h before the temperature was increased to 90°C. EG (10 mL) was added and the resulting solution was further stirred at the same temperature to remove the excess solvent until the solution became a viscous resin. The obtained resin was subsequently dried in an oven at 180°C for 5 h. The sample was then ground with an agate mortar to achieve fine particles and then calcined in a tube furnace. The furnace was programmed to 400°C for 2 h, before heating to 900°C at a ramp speed of 10°C min⁻¹, holding for 4 h and cooling to ambient temperature at 10°C min⁻¹. After calcination, the sample was ground again to ensure very fine particles were obtained.

To produce a material supported with both dysprosium oxide and calcium aluminate, the stoichiometry of the reaction of Al₂O₃ and CaO at high temperatures was analyzed. Several studies describe the production of the calcium aluminate known as mayenite; i.e.,

At temperatures greater than 850°C, mayenite can react with excess CaO to form tricalcium aluminate (Peng et al., 2015); i.e.,

The stoichiometry of these reactions were used to estimate the amount of inert support in the material, and the amount of active CO₂ sorbent was determined based on the percentage of calcination conversion compared to the theoretical mass loss of 43.97% for CaCO₃ (see Table 1). It was assumed that there would be no reaction between the Al(NO₃)₃ and the Dy(NO₃)₃. For comparative purposes, materials composed only of Dy₂O₃, CaO, and CaO supported with calcium aluminate were also prepared (see Table 1).

Material Characterization

Powder X-ray diffraction (XRD) analysis was performed using CuK_α radiation (K_α1 = 1.540598 Å; K_α2 = 1.544426 Å) at a scanning rate of 2.5° min⁻¹ (step size = 0.026°, time per step = 0.31 s) over the 2θ range 15–70°. Diffraction patterns were analyzed with Joint Committee on Powder Diffraction Standards (JCPDS). Crystallite sizes were obtained using the Scherrer calculator function in PANalytical X’Pert HighScore software (Degen et al., 2014). The crystallite sizes were calculated using the peak at 37.4° (the most intense peak at 29° was not evaluated due to an overlap with the peak of Dy₂O₃) using:

where d is the mean crystallite diameter (Å), λ is the X-ray wavelength (Å), 0.89 is the shape factor for CaO, and B is the full width half maximum (FWHM) of the CaO diffraction peak (rad), taking into account instrumental peak broadening.

BET surface area, pore volume and pore size distribution were determined by N₂ adsorption-desorption analysis using a Micromeritics TriStar II 3020 surface area analyzer. All samples were degassed under vacuum for 4 h at 120°C prior to the measurement. Surface area was determined by applying the multipoint BET method, and isotherms were typically analyzed over the relative pressure range of 0.05–0.30. Pore volume and pore size distribution were determined using the BJH adsorption method.

SEM images were recorded by using a Zeiss Sigma VP FESEM. Samples were carbon coated before analysis. Energy dispersive spectroscopy (EDS) mapping was carried out using a Bruker light element SSD EDS detector. TEM images were recorded using a JEOL JEM-1200EXII TEM with STEM and EDS system. Samples were suspended in acetone, sonicated and dispersed on copper grids prior to analysis.

Calcination-Carbonation Cycling Analysis

The extent of conversion with cycling was monitored by thermogravimetric analysis (TGA) using a SETSYS Evolution 1750 TGA-DSC from SETARAM Instrumentation. Testing conditions varied based on calcination atmosphere (N₂/CO₂) and carbonation atmosphere (mixture of CO₂ and N₂/100% CO₂) (cf., Table 2). Experiments in the literature are typically carried out with calcination in N₂ and carbonation under a mixed atmosphere, so these conditions were replicated for comparative purposes. However, a CO₂ atmosphere is potentially more favorable, as using pure CO₂ as the reactor unit atmosphere avoids the need for multiple gas storage, separation and purification units, lowering costs and preventing compression losses (Schaube et al., 2011).

In a typical experiment under 100% CO₂, 18 mg of powder sample was placed into a 100 μL alumina crucible and subjected to 40 cycles of heating to 1000°C and subsequent cooling to 850°C (10°C min⁻¹ heating rate), where the sample was held isothermally for 30 min to allow for carbonation. A constant CO₂ gas flow of 20 mL min⁻¹ was utilized. Experiments such as these with calcination temperatures greater than 900°C are described as “severe” conditions. For an experiment with N₂ as the calcination atmosphere (described as “mild” calcination conditions), the sample was heated to 800°C, held isothermally for 10 min and then cooled to 650°C. The reacting gas was switched to a mixture of 75% v/v N₂ and 25% CO₂ and held isothermally for 30 min to allow for carbonation. The gas was then switched back to N₂ and cycling continued for 40 cycles.

The carbonation conversion of CaO to CaCO₃ was calculated using:

where X(t) is the carbonation conversion extent as a function of time, m(t) is the mass of the sample (g) after time t (min) at the carbonation temperature or under the carbonation atmosphere (t = 30 min), m_i is the initial mass of the sample before carbonation (g), x is the active mass fraction of CaO, m_{X = 1} is the theoretical mass of the sample in grams after 100% carbonation conversion (g; 43.97% mass gain) and M is the molar mass (g mol^–1).

As a means of comparing synthetic materials with different proportions of active material, effective carbonation conversion was calculated. The effective carbonation conversion, X(t)_eff, takes into account the inert portion of the material and was calculated as follows:

For ease of reference, X(t) refers to the “original (carbonation) conversion” and X(t)_eff as “effective (carbonation) conversion” and a comparison of both properties is detailed in the results.

Differential scanning calorimetry was used to determine endothermic and exothermic heats of reaction. Cycling experiments under severe experimental conditions were used to obtain heats of reaction. SETARAM post-processing analysis software was used to integrate the heat flow peaks using the Bezier integration function.

Sintering Model

It has been noted that the practical use of modified synthetic TCES materials will depend on their economic performance, and the impact of inert supports on cost performance has yet to be evaluated in many studies (Valverde, 2013). Prices of inert supports are much higher than natural limestone (Qin et al., 2014), so the improvement in performance of the synthetic TCES materials must be quantified to justify their additional cost. The deactivation of the natural limestone occurs rapidly, which will require a replacement of the materials after a small number of thermal cycles (Grasa and Abanades, 2006). Deactivation of natural limestone was evaluated from cycling experiments performed by Sarrión et al. (2018) using limestone under realistic TCES conditions.

To determine the deactivation of the material with long-term cycling (i.e., assuming the same material is used during the whole lifetime of a CSP plant), the sintering model described by Grasa and Abanades (2006) was used to determine the carbonation conversion (X(N)) after N cycles. The decay trend could be correlated using the parameters deactivation constant (k), residual conversion (X_r) and N; i.e.,

This was used to model loss in conversion for P-CaO and P-CaDy-Al20 (see section “Feasibility Study” and Table 1 for sample composition). The parameters k and X_r were determined using least squares regression. When this model proved unsuitable for modeling sintering over the first 40 cycles (as in the case of P-CaO-Al20 and limestone, referred to as Comm-CaCO₃), a semi-empirical model from Valverde et al. (2017) was used to determine the number of sorbent replacements required over the whole life of a CSP plant [assumed to be 30 years (Steinhagen and Nitsch, 2005)]; i.e.,

where X₁ is the carbonation conversion after the first cycle. In this model it is assumed that the material will be charged and discharged once a day and therefore the number of cycles is identical to the number of days of operation. For reference, it is assumed than replacement will be made when the conversion falls below 20%.

The mass specific storage utilization (kg kWh⁻¹) was evaluated using the experimentally determined exothermic heat of reaction of the candidate materials. To determine the required amount of material over the plant lifetime (μ_Storage), the storage utilization after 30 years was obtained by dividing the number of material replacements (R_{30 years}) by the heat storage capacity after 40 cycles as per:

Results and Discussion

Thermal Cycling and Initial Characterization

Table 2 sets out the experimental conditions and cycling results of synthesized oxides from this work and experiments from published literature. In order to examine the TCES potential, calcination and carbonation conversions were recorded up to 40 cycles (see Table 2). The thermal cycling results under two distinct experimental conditions, severe calcination and mild calcination, are discussed in sections “Cycling Under Severe Calcination Conditions” and “Cycling Under Mild Calcination Conditions,” respectively.

As-synthesized materials were first characterized by XRD, as shown in Figure 1. In addition to peaks of Dy₂O₃, CaO and Ca₃Al₂O₆, the Dy-supported materials show peaks of calcium oxide minerals such as portlandite (Ca(OH)₂) and vaterite (a polymorph of CaCO₃). This indicates that these substances are not completely decomposed during the initial calcination process. Another possibility is that these compounds are formed due to materials reacting with atmospheric moisture and CO₂ post-calcination. Scans taken after cycling (Figure 2) indicate that both portlandite and vaterite decompose during the calcination process, while calcite (CaCO₃) forms during carbonation. Dysprosium carbonate was not detected in the scan, which shows that the dysprosium oxide does not undergo cycling to dysprosium carbonate.

FIGURE 1

FIGURE 2

Cycling Under Severe Calcination Conditions

To evaluate the TCES potential, the materials are cycled under severe calcination conditions (100% CO₂, cycling between 1000 and 850°C). The selected conditions, original conversion and reaction times are gathered in Table 2. The evolution with cycling of original and effective conversion are plotted in Figures 3A,B, respectively. The literature materials selected for comparison are Ca10La-950 (10% La₂O₃, calcined to 950°C) and Ca70Nd-1000 (70% Nd₂O₃, calcined to 1000°C).

FIGURE 3

When comparing the original conversion (Figure 3A and Table 2), it can be observed that the P-CaDy20-CO₂ suffers from a loss of conversion from 94.9% in the first cycle to 51.6% in cycle 20. It is important to note that this material has been synthesized without the addition of Ca₃Al₂O₆. When Ca₃Al₂O₆ is added, the material stability with cycling improves considerably. Addition of 5, 10 or 20% of the Al precursor results in an increase in conversion of 67.6, 82.1, and 84.6%, respectively, after 20 cycles. The latter two materials were cycled for a longer period, with the result that the material with a larger amount of Ca₃Al₂O₆ (P-CaDy-Al20-CO₂) achieves the best stability in this study. This material also achieves the lowest decline in carbonation conversion with thermal cycling, with a decrease of only 8.3% after 40 cycles. The incorporation of Dy₂O₃ was further evaluated by comparing P-CaDy-Al20-CO₂ with P-CaO-Al20-CO₂ (synthesized without the Dy₂O₃ support). The latter shows a loss of conversion from 88.8% in the first cycle to 72.8% in cycle 40, although loss of conversion capacity is less extreme than the material synthesized with only Dy₂O₃ (P-CaDy20-CO₂). The stability of the synthesized materials can be classified in the following order:

• P-CaDy-Al20-CO₂ > P-CaO-Al20-CO₂ > P-CaDy-Al10-CO₂ > P-CaDy20-CO₂.

The materials selected for comparison from literature have the following Ca70Nd-1000 (70% Nd₂O₃, calcined to 1000°C) and Ca10La-950 (10% La₂O₃, calcined to 950°C) (see Table 2). The carbonation conversion achieved by P-CaDy20-CO₂ is higher at 20 and 40 cycles (15.6% and 2.7% higher than Ca10La-950 and Ca70Nd-1000, respectively). It is also necessary to highlight that the amount of inert support contained in Ca70Nd-1000 is much larger as compared to P-CaDy20-CO₂, and the latter slightly improved the carbonation conversion. When CaO was combined with both Dy₂O₃ and Ca₃Al₂O₆ (in P-CaDy-Al20-CO₂) the conversion is 48.6% and 35.7% higher after 20 cycles as compared to Ca10La-950 and Ca70Nd-1000, even though P-CaDy-Al20-CO₂ is calcined under more severe calcination conditions (higher temperature or CO₂ concentration). These results reveal that firstly, the use of Dy₂O₃ improves the stability of CaO, as compared with the supports La₂O₃ and Nb₂O₃, and secondly, that the extra addition of Ca₃Al₂O₆ significantly contributes to an increase in stability with cycle number.

To study the effect of the mass fraction of inert supports, the effective carbonation conversion is shown in Figure 3B. After 40 cycles P-CaDy-Al10-CO₂ and P-CaDy-Al20-CO₂ outperform all the materials in this study, as well as in the literature references. When 10% aluminium precursor is added (P-CaDy-Al10-CO₂), the effective carbonation conversion drops from 66.5% in cycle 20 to 51.8% in cycle 40, and the slope of the conversion decay indicates that the carbonation conversion is not yet stabilized after 40 cycles. However, the addition of 20% aluminium precursor (P-CaDy-Al20-CO₂) helps to maintain the effective carbonation conversion from 56.4% in cycle 1 to 51.3% in cycle 40. The best performing material P-CaDy-Al20-CO₂ has stabilized after 40 cycles with 82.7% original and 51.3% effective conversion capacities (see Figures 3A,B, respectively). In comparison, the Nd₂O₃ and La₂O₃ supported materials from the literature show much lower effective carbonation conversions after 40 cycles. Comparing effective carbonation conversion gives a more realistic picture of material performance, particularly in the case of Ca70Nd-1000, which contains 70% inert material. Additionally, only the Ca10La-950 is tested under 100% CO₂, while Ca70Nd-1000 is calcined under a N₂ atmosphere (see Table 2). Testing under pure CO₂ displaces the reaction equilibrium point to higher temperatures and is known to accelerate sintering and loss of conversion (Stanmore and Gilot, 2005). Therefore, the higher carbonation conversions of the materials in this work are particularly noteworthy, considering that the experimental conditions are more severe than those in the literature. Good performance under 100% CO₂ is also highly relevant to TCES, as these more realistically represent reactor conditions (Schaube et al., 2011).

Cycling Under Mild Calcination Conditions

To further evaluate the materials and compare with literature, the synthesized material which performed best under severe conditions (P-CaDy-Al20; cf., section “Cycling Under Severe Calcination Conditions”) was tested under mild calcination conditions (100% N₂ calcination, 75:25 N₂:CO₂ carbonation, cycling between 800 and 650°C). As for section “Cycling Under Severe Calcination Conditions,” the selected conditions, original conversion and reaction times are gathered in Table 2, while original and effective carbonation conversion are plotted in Figures 4A,B, respectively. The literature materials selected for comparison are Ca70Nd-800/900 (70% Nd₂O₃, calcined to 800/900°C), Ca10Yb-800/900 (10% Yb₂O₃, calcined to 800/900°C), and Ca10La-850 (10% La₂O₃, calcined to 850°C).

FIGURE 4

When examining the original conversion (Figure 4A) it can be observed that the P-CaDy-Al20-N₂ achieves ∼100% carbonation conversion in the first cycle, dropping to 76% in cycle 40. Taking into account the fraction of inert support (Figure 4B), P-CaDy-Al20-N₂ achieves 62% carbonation conversion in the first cycle, and this drops to 55% carbonation conversion in cycle 40.

Compared to P-CaDy-Al20-CO₂ (Figures 3A,B) the carbonation conversion of P-CaDy-Al20-N₂ is initially greater, but this drops off with cycling and the material does not reach stable conversion after 40 cycles (Figures 4A,B). This could be due to the phenomenon of “self-reactivation” under CO₂ as compared to calcination under N₂ (Manovic and Anthony, 2005). It is well known that calcining CaO under 100% CO₂ displaces the reaction point to higher temperatures, and is known to accelerate sintering and loss of conversion (Stanmore and Gilot, 2005). Thermal cycling causes the development of a hard inward skeleton of low porosity, less reactive CaO, surrounded by a softer layer of reactive, porous CaO. This hard skeleton is hypothesized to keep the pore structure stable during cycling while the external soft skeleton is regenerated in each re-carbonation (Manovic and Anthony, 2005). The residual CO₂ uptake capacity was determined by the CaO skeleton structure, which is heavily influenced by the calcination temperature (Kierzkowska et al., 2013). Manovic and Anthony found that pre-treatment of limestone to temperatures greater than 1000°C increased residual conversion (Manovic and Anthony, 2005), which is reflected in this study.

P-CaDy-Al20-N₂ was then compared with materials from literature experiments. As shown in Figure 4A, P-CaDy-Al20-N₂ outperforms the La₂O₃ and Yb₂O₃ supported materials, but falls short of the Nd₂O₃ supported material. When considering effective carbonation conversion (Figure 4B), P-CaDy-Al20-N₂ clearly outperforms the Nd₂O₃-supported sample, which is predominantly composed of inert material (70%). It also outperforms the La₂O₃ supported material and is predicted to outperform the Yb₂O₃-supported material, which shows poor stability. P-CaDy-Al20 is therefore seen to perform well and exhibit high performance under both mild and severe experimental conditions. Its performance is best under 100% CO₂, conditions which are most relevant for TCES.

Characterization Results

Table 3 presents the crystallite sizes of the synthesized materials obtained using the Scherrer equation. Crystallite sizes range from 58 to 90 nm in the materials in their as-synthesized state. Using XRD results, similar crystallite sizes were initially obtained for P-CaDy20 and the supported material P-CaDy-Al20 (87 and 83 nm, respectively). However, a significant difference in the crystallite sizes is calculated after 40 calcination and carbonation cycles. Average crystallite size increases to 201 nm for P-CaDy20, while P-CaDy-Al20 reaches 128 nm after 40 cycles, which reflects its resistance to sintering.

Table 4 shows the results of BET and pore size analysis for the materials, as synthesized and after 40 cycles of calcination and carbonation cycling. Measurements show that supporting CaO with Dy₂O₃ results in a significant improvement in the retention of surface area. P-CaDy-Al20-c shows a reduction of surface area of only 3.4 m² g⁻¹, as compared to P-CaO, which has almost negligible surface area after 40 cycles.

SEM images (Figure 5) show that the synthesized materials P-CaDy20 and P-CaDy-Al20 display a porous structure, indicative of high surface area. The morphology of Dy₂O₃ is seen to be more jagged. In Figures 5a,b it can be seen that the P-CaDy20 sinters significantly after 20 cycles. Figure 5b shows that the material clumps together, losing its fluffy, porous nature and develops rounded particle edges. However, with the addition of an alumina support in P-CaDy-Al20, less sintering is evident (Figures 5c,d). The TEM images show the increased porosity of P-CaDy-Al20 (Figures 6d–f) compared to P-CaDy20 (Figures 6a–c). Note the dark regions in these figures which indicate the presence of Dy₂O₃.

FIGURE 5

FIGURE 6

Figure 7 displays EDS mapping for the as-synthesized materials, unsupported (P-CaDy20; Figures 7A,C) and supported (P-CaDy-Al20; Figures 7B,D). Figure 7A shows that the elements of P-CaDy20 are unevenly distributed across the material, particularly dysprosium. However, Figure 7B shows a much more thorough homogeneous distribution. In particular, the red dysprosium is barely visible due to complete overlap with the green calcium, which reflects the even dispersion of Dy₂O₃ across the CaO. Particle growth after cycling can be compared between the supported and unsupported materials. Figure 7C shows that P-CaDy20 exhibits significant particle growth after 40 cycles, while P-CaDy-Al20 resists sintering (Figure 7D).

FIGURE 7

Theories on how inert supports act to prevent sintering include the grain boundary “pinning effect” and the effect of densification. Adhesion of the support particle to the grain boundary was postulated to exert a pinning effect and hence provide a drag force to oppose grain growth (Li et al., 2013). Only the support particles on the grain boundaries will exert a pinning force. In this way, the support particles act as a “metal skeleton” – spacers to separate the CaO/CaCO₃ particles (Hu et al., 2015). Alternatively, inert spacers are suggested to suppress densification and loss of micro- or meso-porosity during repeated calcinations (Zhao et al., 2014). As CaCO₃ has a lower density than CaO, this leads to pore closure of unreacted CaO and increased diffusional resistance of CO₂. If CaO is supported with an inert support with unchanging volume, sorbent expansion during carbonation will be decreased, keeping pores open for CO₂ diffusion through the product layer (Jing et al., 2017).

Both explanations can potentially explain the improved performance of P-CaDy-Al20. TEM imaging reveals greater pore volume in P-CaDy-Al20 compared to P-CaDy20 (Figures 6d–f), which is also retained after cycling. EDS mapping also shows evidence of the mitigation of sintering in P-CaDy-Al20 as opposed to P-CaDy20 (Figure 7). The light blue aluminate domains throughout the material and around the grain boundaries could be indicative of the “pinning” effect of calcium aluminate.

Heat Storage Capacity and Comparison With Other TCES Materials

The heat storage capacities of the synthesized materials were evaluated using DSC analysis during thermal cycling and compared with experimental data from literature (see Table 5). Figure 8 shows the variation of heat storage capacity with cycling, with Figure 8A showing that stable readings were obtained for P-CaDy-Al20. While the heat storage capacity of P-CaO-Al20 is initially higher due to the slightly higher amount of active CaO in P-CaO-Al20 (cf., Table 1), P-CaDy-Al20 exhibits a greater stability measured with cycling for both endothermic and exothermic processes (cf., Figure 3). After 40 cycles, the heat storage capacity of P-CaDy-Al20 is 25% greater than P-CaO-Al20 without Dy₂O₃. The greater exothermic heat flows in P-CaDy-Al20 are due to enhanced stability and are linked directly to enhanced carbonation conversion with cycling (cf., Figure 3). Cycling of pure Dy₂O₃ ascertained that the material does not act as a CO₂ sorbent, and without the inert support calcium aluminate (as in P-CaDy20; cf., Figure 8B), the material is unstable. However, the synergistic combination of Dy₂O₃ and Ca₃Al₂O₆ as inert supports achieves excellent results.

FIGURE 8

Table 5 compares the experimental results to heat storage capacities of other materials in published literature except for CuO (Alonso et al., 2015) and commercial CaCO₃, for which the values have been obtained using thermochemical data. P-CaDy-Al20 and P-CaO-Al20 achieve the highest heat of reaction values, even after 40 reaction cycles. Pure CaCO₃ has a calcination heat of reaction of 1624.6 kJ kg⁻¹ [according to simulations performed using HSC Chemistry 8^® (Roine, 2018)], but this is predicted to drop to 81 kJ kg⁻¹ after 40 cycles, taking into account loss of reactivity using a sintering model (see section “Sintering Model”). As compared with other well-investigated thermochemical systems, such as Co₃O₄/CoO (Carrillo et al., 2014), BaO (Fahim and Ford, 1983), CuO (Alonso et al., 2015), Mn₂O₃/Mn₃O₄ (Carrillo et al., 2014), (Mn_0.1Fe_0.9)₂O₃ (Carrillo et al., 2015), the spinel (Mn_0.33Fe_0.67)₂O₃ (Al-Shankiti et al., 2019; Hamidi et al., 2019), (Co_0.867Fe_0.133)₃O₄ (Block et al., 2014), and (Co_0.99Mn_0.01)₃O₄ (Carrillo et al., 2014), P-CaDy-Al20 has the largest exothermic heat storage capacity after a longer cycling period. After 40 cycles, this heat of reaction (582.2 kJ kg⁻¹) is 3.3 times greater than (Mn_0.33Fe_0.67)₂O₃ (Hamidi et al., 2019), 18% higher than the well-known Co₃O₄/CoO redox pair (Carrillo et al., 2014) and 7.3 times higher than Mn₂O₃/Mn₃O₄ (Carrillo et al., 2014). Therefore, it can be concluded that the materials P-CaDy-Al20 and P-CaO-Al20 have the best performance so far found in literature for this type of small laboratory scale analysis. Further work should be perfomed at reactor level to compare the materials in this work with reactor-scale tests in published literature (Tescari et al., 2013).

Feasibility Study

Figures 9A,B show the application of sintering models to the first 40 carbonation cycles of experimental data (cf., sections “Material Characterization” and “Calcination-Carbonation Cycling Analysis”). Using the sintering model with the greatest accuracy (Table 6), the long-term performance of selected synthesized materials was modeled (Figure 9C).

FIGURE 9

A feasibility assessment of the selected synthesized materials and commercial CaCO₃ is presented in Table 6. The indicated sintering models were used to determine the number of cycles for carbonation conversion to fall below 20%. This cut-off has been suggested as the minimum carbonation conversion capacity to allow for optimum plant efficiency using a pressurized fluidized bed combustor as the carbonator (Prieto et al., 2016). If carbonation conversion drops below this capacity, it will need to be replaced with fresh material.

The sintering models determine that residual carbonation conversion does not drop below 20% for P-CaDy-Al20, even after 30 years of continuous cycling, whereas unsupported P-CaO would need to be replaced after seven cycles and Comm-CaCO₃ would need to be replaced every six cycles. This would incur additional operation and maintenance costs on top of the cost required to replace the material.

When evaluating the mass specific storage utilization (μ_Storage) after 40 charge and discharge cycles, the best performing materials are P-CaDy-Al20 and P-CaO-Al20, with storage densities of 6.2 and 7.8 kg kWh⁻¹, respectively. When considering the amount of material required after replacement over the CSP plant lifetime, the improved storage utilization of P-CaDy-Al20 is even more apparent. After 30 years, it is expected to retain a storage utilization (μstorage) as low as 6.2 kg kWh⁻¹, compared to 81 tons kWh⁻¹ for commercial CaCO₃ (Table 6). This is due to its superior stability and extremely high residual carbonation conversion. These results justify the additional cost of inert supports for the synthesized material P-CaDy-Al20 and indicate its suitability for large-scale energy storage applications.

Conclusion

A CaO-based material supported with Ca₃Al₂O₆ and Dy₂O₃ shows excellent energy sorption cycling under a CO₂ atmosphere. The main benefits are due to its retention of high surface area compared to CaO and the addition of anti-sintering properties, even under an atmosphere which accelerates sintering. A conversion capacity of 82.7% is retained after 40 cycles under severe calcination conditions while other materials in the literature show high deactivation. The retention of conversion capacity is not the only feature that makes the material promising for TCES. A further feasibility study found that the exothermic heat of reaction obtained (582.2 kJ kg⁻¹) is up to seven times higher than other TCES systems (like Mn₂O₃/Mn₃O₄ redox cycle). In addition, a sintering model was applied to evaluate the specific storage utilization. In this study it was found that 6.2 kg kWh⁻¹ is required for the CaO supported with Ca₃Al₂O₆ and Dy₂O₃, while for commercial limestone 81 tons kWh⁻¹ will be needed over 30 years (a common CSP plant life). This is because the conversion capacity of commercial limestone drops below 20% after six thermal cycles (or 6 days assuming one cycle per day) and this implies the need for 1825 replacements over a common CSP plant life. This initial feasibility study shows that despite the additional cost of the supports, their addition is beneficial for the stable and long-term performance of the storage system.

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