Influence of MnO2-Birnessite Microstructure on the Electrochemical Performance of Aqueous Zinc Ion Batteries

Abstract

K_xMnO₂ materials with birnessite-type structure are synthetized by two different methods which make it possible to obtain manganese oxides with different degrees of crystallinity. The XPS results indicate that the sample obtained at high temperature (KMn8) exhibits a lower oxidation state for manganese ions as well as a denser morphology. Both characteristics could explain the lower capacity value obtained for this electrode. In contrast, the sample obtained at low temperature (KMn4) or by hydrothermal method presents a manganese oxidation state close to 4 and a more porous morphology. Indeed, in this case higher capacity values are obtained. At current density of 30 mA g⁻¹, the KMn8, KMn4, and HKMn samples display a capacity retention of 88, 82, and 68%, respectively. The higher capacity loss obtained for the HKMn compound could be explained considering that the incorporation of Zn²⁺ in the structure gives rise to the stabilization of a ZnMn₂O₄ spinel-type phase. This compound is obtained in the discharge process but remains in the charge stage. Thus, when this spinel-type phase is obtained the capacity loss increases. Moreover, the stabilization of this phase is more favorable at low current rates where 100% of retention for all samples, before 50 cycles, was observed.

1. Introduction

Today’s growing global demand for energy requires greener and more sustainable storage technologies. In the field of energy conversion and storage, lithium-ion batteries have successfully fulfilled a great proportion of global storage demand, but these devices present important safety and environmental drawbacks [1]. The search for new low-cost and environmentally friendly multivalent systems that offer high performance is thus a current challenge. In this context, zinc-ion batteries (ZIBs) meet the requirements to be a true alternative for various devices: high theoretical specific capacity, the use of aqueous electrolytes, the natural abundance and safety of zinc [2]. In addition, ZIBs can be easily fabricated in an open-air environment, which significantly reduces their overall production cost [3]. Nevertheless, it is still necessary to overcome several fundamental and practical problems for the extensive use of ZIBs to become the norm [4,5,6]. Aqueous ZIBs are secondary Zn-based batteries, in which the storage and conversion of energy is realized through the transfer of Zinc cations between the cathode and the anode. Thus, one of the challenges is related to the increase in electrostatic interactions that inhibit the diffusion of Zn²⁺ within the electrode structure, and hence, there is a shortage of electrode materials capable of fast, reversible (de)intercalation of Zinc ions [7]. Moreover, intercalation of multivalent ions can also be impeded by hydrated cations which have to be desolvated at the electrode–electrolyte interface. Another issue that has received a great attention from the scientific community is the significant challenge of H⁺/Zn²⁺ co-intercalation in aqueous media.

In this sense, our work focuses on various ZIBs built with non-expensive manganese oxides with birnessite-type structure as cathodes, aqueous and innocuous electrolyte, and Zn as anode. The electrolyte employed was a solution of 0.1 M Mn(II) nitrate and 2 M Zn(II) nitrate. Thus, K_xMnO₂ materials employed as cathodes are prepared by straightforward, low cost and green methods in which tuned morphologies are obtained. Surface modification of the manganese oxide electrode is considered a viable strategy to improve electrochemical properties in aqueous zinc-ion batteries. Therefore, the paper aims to analyse the influence of structural features and particle morphology in the electrochemical performance of different birnessite-type manganese oxides.

2. Materials and Methods

2.1. Synthesis of Materials

Two methods are employed in the synthesis of manganese oxides to be used as cathodes in ZIBs.

(1) Thermal reduction: KMnO₄ (Sigma Aldrich, Madrid, Spain, 99%) is homogeneously dispersed in a porcelain vessel and heated at temperatures of 400 and 800 °C for 6 h at 10 °C/min. After calcination, each material is washed with deionized water to remove soluble salts (potassium manganates) formed during the process. These samples hereinafter are called as KMn4 and KMn8, respectively.

(2) Hydrothermal method: the manganese oxides with birnessite structure are prepared from 20 mL of 0.3 M KMnO₄ (Sigma Aldrich, Madrid, Spain, 99%). This solution is transferred to an autoclave and kept at 180 °C for 10 h. Once room environmental temperature was reached, the powder obtained was filtered and dried on a stove at 80 °C for 12 h. This sample is hereinafter referred to as HKMn.

2.2. Characterization Techniques

X-ray powder diffraction (XRD) patterns were registered at room temperature with a PANanalytical X’PERT POWDER diffractometer using Cu (Kα) radiation with λ = 1.5406 Å. Data were collected in the range 5° ≤ 2θ ≤ 120° range with a step of 0.0167° and analysed by the Rietveld profile method [8] using the WinPLOTR/Fullprof suite program [9].

High resolution transmission electron microscopy (HRTEM) was performed in a JEOL 300FEG. The composition of the obtained materials was established by semi-quantitative chemical analysis using energy dispersive X-ray spectroscopy (EDXS). The samples were prepared by crushing the powders under n-butanol and dispersing it over copper grids covered with a porous carbon film. Scanning electron microscope (SEM) images and corresponding EDXS spectra were obtained with a JEOL JSM 6335F microscope. Samples were mounted on SEM stubs using carbon adhesive and sputter-coated gold. Thermogravimetric analyses (TGA) were carried out under nitrogen by a Pyris thermogravimeter (PerkinElmer, Waltham, MA, USA). The analyses were carried out at a heating/cooling rate of 10 °C min⁻¹.

XPS studies were performed on a PHI Versa Probe II spectrometer (Physical Electronics, Minneapolis, MN, USA) with monochromatic X-ray Al K_α radiation (100 μm, 100 W, 20 kV, 1486.6 eV) and a dual-beam charge neutralizer. The instrument work function of the spectrometer was calibrated using Cu 2p_3/2 (932.7 eV), Ag 3d_5/2 (368.2 eV) and Au 4f_7/2 (84.0 eV) photoelectron lines. The collected XPS spectra were analysed using PHI SmartSoft software (version 9.6.0, PHI, Minneapolis, MN, USA) and processed with MultiPak 9.1. Charge referencing was done against the adventitious carbon C 1s signal (284.8 eV). Recorded spectra were fitted using Gauss–Lorentz curves.

The electrochemical tests of half cells were performed in Swagelok-type cells, using graphite paper as current collector (for both anode and cathode electrodes), Zn disk as the anode and Whatman GF/D borosilicate glass fibre sheets impregnated with solutions of 2 M ZnSO₄·7H₂O and 0.1 M MnSO₄·H₂O (Sigma-Aldrich, St. Louis, MO, USA). The synthesized samples were mixed with carbon SP (from Imerys Graphite & Carbon, Bironico, Switzerland) and sodium alginate in deionized water with mass proportions 80:10:10, respectively. The resultant slurry was coated on to the graphite paper and dried in the air overnight. The resulting electrodes had an active material loading of about 1–3 mg.

Electrochemical testing was done using a Biologic 815 potentiostat. Cyclic voltammetry (CV) and galvanostatic charge and discharge (GCD) tests were conducted in a potential window between 0.8 and 1.8 V. Different scan rates were applied for CV testing, as well as several different applied specific currents were used for GCD testing. The applied current densities were normalized to the mass of manganese oxide on the electrode.

3. Results and Discussion

3.1. Materials Characterization

The XRD patterns of all samples are showed in Figure 1. Basal reflections at 12.5 and 25.1°, characteristic of the birnessite layered structure are observed for all samples. The reflections at higher 2θ-values exhibit some differences, indicative of structural dissimilarity between the samples. Thus, the wide maxima at 2θ~36.8° (2.44 Å) and 2θ~66.3° (1.41 Å) for KMn4 indicate a birnessite with turbostractic structure. In contrast, all reflections of the KMn8 could indexed to a hexagonal unit cell with a = 2.864(3) and c = 14.274(2) Å. On the other hand, HKMn maxima are coherent with a rhombohedral symmetry and cell parameters a = 2.846(9), 21.751(6) Å.

Table 1 gathers relevant crystallographic data obtained from Rietveld refinements of XRD data for KMn8 and HKMn. The corresponding profiles are shown in Figure 2. The structural models for both samples are also included (insets), evidencing the differences between them. Whereas the unit cell of KMn8 can be described as two-layer hexagonal (2H), the HKMn unit cell is three-layer hexagonal (3H). Thus, the close-packing notation for the 2H model is: AbC (water)-CbA (water)-AbC(water), and for the 3H model is: AbC(water)-CaB(water)-BcA(water), where A, B, C represent the oxygen positions and a, b, c refer to Mn positions [10,11]. The potassium ions and water molecules share the interlayer space as shown in Figure 2.

Vertical bars indicate Bragg permitted reflections. Insets show corresponding structural models: layers of MnO₆ octahedra are represented in pink; water molecules and potassium cations are situated between layers.

EDX analysis indicated the presence of potassium in all the samples but in different concentration. Thus, examination of a representative number of crystals in each case led to mean different formulae. For KMn4 and KMn8, 0.3 K per formula was obtained. In the case of the HKMn sample, mean composition K_0.03MnO₂ was obtained, though in some crystals the obtained ratio was 0.3:1. Therefore, the samples prepared by different methods seem to retain different amounts of K in the interlayer space.

In addition, the thermogravimetric analysis in the 50–600 °C temperature range (Figure S1) displays three regions where decomposition takes place. The initial weight loss up to 120 °C can be associated with evaporation of surface-adsorbed water, whereas the second region, up to 200 °C, can be attributed to the dehydration of the interlayer water. Finally, the weight loss obtained when the material is heated above 250 °C, is usually associated with oxygen loss [12]. Furthermore, when the material is heated up to 600 °C, the HKMn is transformed into a 2 × 2 channel structure, as previously suggested [13]. Such changes are shown in the XRD diagram of the residue (Figure S1b,c). However, the XRD profiles of the KMn4 and KMn8 residues indicated a mixture of phases in which birnessite and a structure with 2 × 2 channel are present. Therefore, the amount of K between octahedra layers seems to be key in the thermal stability of birnessite structure. Therefore, in principle, hydrothermal method led to phases where the K amount is smaller than the obtained by thermal treatment.

In order to know the Mn oxidation state, XPS experiments were carried out. The Mn 2p core-level spectra for all compositions are shown in Figure 3 and the corresponding BE values are given in Table 2. The BEs of the Mn 2p_1/2 and Mn 2p_3/2 signals are given by the positions of the maxima of the main peaks. The asymmetric Mn 2p_3/2 main peak is located at 642.3–642.6 eV with a (2p_3/2–2p_1/2) splitting of 11.8–11.9 eV. These values are closer to the BE of Mn 2p_3/2 peaks reported for MnO₂ (642.2 eV) [13].

Analysis of the 3s region is more useful to assess the oxidation state of manganese, due to mainly the exchange interaction between the 3s and 3d electrons [14,15]. The 3s splitting (Table 2) suggests that the samples have a Mn³⁺ and Mn⁴⁺ mixture. The values of Mn average oxidation state in KMn4, KMn8 and HKMn are gathered in Table 2 and were obtained as suggested by Beyreuther at al. [16] taking into account the doublet separation from Equation (1).

υ_Mn = 9.67 − 1.27ΔE_3s/eV(1)

where υ_Mn is the average oxidation state and ΔE_3s splitting magnitude of 3s.

Therefore, taking into account the above results, the sample obtained at high temperature presents the highest amount of Mn(III). On the other hand, the sample prepared by hydrothermal method probably contains oxygen vacancies. As previously stated, the K amount in the formula of HKMn is considerably less than in the other samples [17].

The material morphology has a great influence on the electrochemical behaviour and therefore was analyzed by SEM and HRTEM. Some representative images are depicted in Figure 4. KMn8 (Figure 4c,d) consists predominantly of large micrometer-sized crystals exhibiting well-defined crystallographic faces whereas KMn4 (Figure 4a,b) exhibits cloud-like particles with diameters ranging between 175 and 260 nm. These large particles appear as aggregates of smaller individual particles with diameter close to 20 nm. On the other hand, HKMn (Figure 4e,f) present flower-like nanostructures, the individual nanoflowers are micro-sized and comprise a large number of thin nanosheets with a thickness of 15 nm. Moreover, striations along [1] orientation are clearly seen with spacings of ~7 Å in all samples.

3.2. Electrochemical Behaviour

Figure 5 shows charge–discharge profiles of the three prepared samples at 30 mA g⁻¹, between 1.8 and 0.8 V. The observed behaviour of the different charge-discharge profiles of the three samples, KMn4, KMn8, and HKMn, are similar to that reported previously in the literature for Zn-manganese oxide batteries [18]. Figure 5b gathers the efficiency and specific capacity values for all samples. It can be observed that at current density values of 30 mA g⁻¹, all electrodes achieve capacity values lower than the theoretical one (308 mA h g⁻¹). In the initial cycles, the following order in the capacity values is observed: KMn8 < KMn4 < HKMn. This result agrees with the average oxidation state obtained by XPS as well as the amount of K in the interlayer space commented above. Moreover, after 50 cycles, the specific capacity reached are 90, 105 and 110 mA h g⁻¹, which mean capacity losses of 12, 14, and 32% for KMn8, KMn4, and HKMn, respectively.

Figure 6 shows the CV curves for assembled ZIBs using different currents for KMn8, KMn4 and HKMn. Their general aspect is similar to that previously found in other Mn-oxide ZIBs [19,20,21]. From the second cycle, two reduction peaks appear at 1.30 and 1.20 V. An oxidation peak at 1.55 V and a small shoulder at 1.65 V are also observed at lower speeds, i.e., 0.1–0.3 mV s⁻¹. The voltage values of each peak are dependent on the scan rate and the sample morphology. Thus, at higher rates (0.7 and 1.1 mV s⁻¹) the CV curves exhibit one strong cathodic peak located at 1.28 V and the other peak is now seen as a shoulder at 1.18 V and even disappear for the sample HKMn. In the same way the anodic peak at 1.55 V disappears and the shoulder at 1.65 hexagonal (2H) increases in intensity.

This gradual voltage change can be attributed to the ion diffusion [22]. At the discharge processes, as the CV rate increases the high-voltage peak remains present and even more intense (due to H⁺ insertion), while the low-voltage peak gradually decays (related to Zn²⁺ reaction).

In order to study the performance at high density current, the three samples were cycled at a rate of 300 mA g⁻¹. Corresponding galvanostatic curves as well as capacity and efficiency versus cycle number are shown in Figure 7. In agreement with above statement, in the discharge stage the second plateau at this high speed is hardly seen for the three samples, which is related to Zn²⁺ insertion. It is only weakly appreciated in the HKMn sample, in which Zn²⁺ can be accumulated in the hollows between the leaves of the flower-like morphology. In addition, the capacity values obtained are in the same order than at low current density, i.e., KMn8 < KMn4 < HKMn. However, a different tendency is observed for capacity losses, which are practically negligible after 50 cycles.

The slight increase of capacity observed in Figure 5 and Figure 7 can be due to the Mn²⁺ present in the electrolyte, that can be related to deposition of MnO₂ during the cycle as has been evidenced in the literature [23,24].

As has been suggested [25], the high voltage plateau in the discharging process (i.e., at 1.4 V) is due to a conversion reaction between MnO₂ and H⁺ leading to MnOOH as intermediate, which is dissolved in acid medium through a disproportion. Therefore, the reductive reaction can be described as follows:

MnO₂(s) + H⁺(aq) + 1e⁻ → MnOOH(s)(2)

MnOOH(s) + H⁺(aq) → ½Mn²⁺(aq) + ½MnO₂(s) + H₂O(l).(3)

In consequence, during the discharge process both dissolved Mn²⁺ and solid MnO₂ will form.

Moreover, the H⁺ are consumed in this reaction. The above reaction (2) takes place due to that Zn²⁺ (aq) provides the hydrogen ions needed as follows:

[Zn(H₂O)_x]²⁺ → [Zn(H₂O)_x−1(OH)]⁺ + H⁺(aq)(4)

At the same time, the precipitation of zinc hydroxide sulphate (ZHS) occurs.

4Zn²⁺(aq) + 6OH⁻(aq) + SO₄²⁻(aq) + 5H₂O(l) → Zn₄(OH)₆(SO₄).5H₂O(s)(5)

XRD data was collected for KMn4 electrode after three cycles, and the XRD profiles of the sample discharged and charged are shown in Figure 8. In the XRD diagram corresponding to the discharged electrode, the peaks located at 12.3° and 24.8°(2θ) are characteristic of birnessite (PDF 1-080-1098). The other maxima that appear in the profile could be assigned to Zn₄(OH)₆(SO₄)·5H₂O (PDF-044-0673) phase (ZHS). However, at 2θ = 36.4° a new maximum appears, which corresponds to the most intense maximum of the ZnMn₂O₄ spinel. Therefore, the second plateau at 1.3 V can be related to the reaction between MnO₂ and Zn²⁺ giving rise to the spinel-type compound:

2MnO₂ + Zn²⁺ + 2e⁻ → ZnMn₂O₄(6)

The XRD pattern of KMn4 electrode charged presents practically the same peaks as those observed in the original diffraction profiles. A slight difference can only be appreciated, the maximum at 2θ = 36.4° is slightly more intense, because of ZnMn₂O₄ phase which was obtained in the discharge process. Therefore, the second plateau at 1.3 V is only partially reversible. As the number of cycles increases, the amount of spinel phase increases, and this could explain the loss of capacity.

Therefore, the global reaction can be formulated as follows:

3/2MnO₂(s) + 2H⁺(aq) + ½Zn²⁺(aq) + 2e⁻ → ½Mn²⁺(aq) + ½ZnMn₂O₄(s) + H₂O(l) (7)

Zn → Zn²⁺ + 2 e⁻(8)

3/2MnO₂(s) + 2H⁺(aq) + Zn(s) → ½Mn²⁺(aq) + ½ZnMn₂O₄(s) + H₂O(l) + ½Zn²⁺(aq)(9)

On the contrary, in the charge process the reverse reaction takes place, i.e., the Mn²⁺ is oxidized to MnOOH, which in acid environment disproportionates leading to MnO₂ birnessite:

Mn²⁺ + 2H₂O → MnOOH + 3H⁺ + 1e⁻(10)

MnOOH + 1H⁺ → ½MnO₂ + ½Mn²⁺ + H₂O(11)

Zn²⁺ + 2 e⁻ → Zn(12)

Mn²⁺(aq) + 2H₂O + Zn²⁺(aq) → MnO₂(s) + 4H⁺(aq) + Zn(s)(13)

Taking into account the mechanism indicated above, some conclusions could be established. First, charge–discharge process leads to the ZnMn₂O₄ spinel, which is created in the discharge process, but it is not reversibly transformed to MnO₂ in the charge process. Thus, ZnMn₂O₄ seems to be present in charge stage (Figure 8). Therefore, the irreversibility obtained in aqueous Zn-ion batteries is related to the ZnMn₂O₄ compound [26], which is obtained in the second plateau, i.e., at low potential (1.3 V). At low density current, 30 mA g⁻¹, both plateaux appear and when the number of cycles grows up, the second plateau becomes smaller. The order in the length of this plateau is as follows: KMn8 < KMn4 < HKMn. The capacity loss for these materials goes on the same sequence. Finally, this plateau is hardly seen at high density current (300 mA g⁻¹), then after 50 cycles the loss capacity is practically negligible.

Moreover, this result has been supported by XRD data (Figure 9) of the HKMn electrode cycled at 30 mA g⁻¹ rate until the battery stopped working. All maxima that appear were identified as the phase ZnMn₂O₄, neither maximum of ZHS or birnesite-type structure was observed.

4. Conclusions

Manganese oxides with birnessite-type structure have been synthetized by two different methods: thermal treatment and hydrothermal method. Both syntheses were carried out from a low-cost material (KMnO₄). The thermal decomposition at temperatures of 400 and 800 °C made it possible to obtain K_xMnO₂ birnessite with different crystallinity degree. Moreover, XPS data indicated that the sample obtained at higher temperature presents on the surface a lower amount of Mn⁴⁺ that the other derivatives. In relation to structure characterization obtained by powder X-ray diffraction, KMn4 presents a turbostractic structure whereas KMn8 and HKMn have hexagonal and rhombohedral symmetries, respectively. The morphologies obtained by SEM and HRTEM for KMn8, KMn4, and HKMn samples shown well-defined crystals, cloud-like particles with aggregates and a flower-like nanostructure, respectively.

The sample obtained at high temperature (KMn8) exhibits a lower oxidation state as well as a denser morphology, both characteristics are related to the obtained low-capacity value. The Zn²⁺ insertion is very small at low density current and negligible at high density current, which seems to be a key factor of capacity retention. On the other hand, in the samples obtained at low temperature (KMn4) or by means of hydrothermal method, Mn cations have an oxidation state close to 4 and their morphologies allow Zinc ions to have a better accessibility towards birnessite-type structure. The incorporation of Zn²⁺ in the structure gives rise to the ZnMn₂O₄ spinel and this process implies that some links must be broken, and at the same time others must be set up. When the spinel-like ZnMn₂O₄ structure is obtained capacity retention reduces, which is favorable at low speeds. In consequence, the best result is obtained when the sample presents a great accessibility and high density current where ZnMn₂O₄ compound would not have enough time to form.

Author Contributions

Conceptualization, M.L.L. and E.R.-C.; methodology, I.Á.-S.; validation, M.L.L., E.R.-C. and I.Á.-S.; investigation, P.A. and D.A.G. and E.R.-A.; writing—original draft preparation, M.L.L. and E.R.-C.; writing—review and editing, M.L.L., I.Á.-S. and E.R.-C. visualization, P.A.; supervision, M.L.L.; project administration, M.L.L. funding acquisition, I.Á.-S. All authors have read and agreed to the published version of the manuscript.

Funding

This work has been supported by the Spanish Ministry of Economy and Competitiveness (MINECO) through project MAT2017-84118-C2-2-R and Spanish Ministry of Science Innovation and Universities trough project RTI2018-099668-B-C22, which have not played any role in any aspect regarding the study design, the collection, analysis and interpretation of data, the writing of the report, or the decision to submit the article for publication.

Institutional Review Board Statement

Not applicable.

Informed Consent Statement

Not applicable.

Data Availability Statement

The following are available on line Figure S1. (a) Thermogravimetric analysis under N2 for all samples. (b) XRD profile of KMn8 residue, the maxima were assigned to a mixture of phases: birnessite and K1.33Mn8O16; (c) XRD profile of the HKMn residue, the maxima were indexed to K1.33Mn8O16. Table S1. Weight loss from ATG data (%) and Structural formulas for birnessite-type material obtained from EDX and ATG data.

Acknowledgments

The authors would like to thank Imerys Graphite & Carbon who kindly provided the carbon black. In addition, authors are grateful to the CAI centers of UCM (XRD and electron microscopy).

Conflicts of Interest

The authors declare no conflict of interest. The funders had no role in the design of the study; in the collection, analyses, or interpretation of data; in the writing of the manuscript, or in the decision to publish the results.

Publisher’s Note: MDPI stays neutral with regard to jurisdictional claims in published maps and institutional affiliations.

Figures and Tables

Figure 1. XRD patterns of (a) KMn4, (b) KMn8 and (c) HKMn.

Figure 2. Calculated (line), experimental (dot) and difference (bottom line) Rietveld profiles for (a) KMn8 and (b) HKMn.

Figure 3. XPS spectra of KMn8, KMn4 and HKMn: (a) Mn 2p region and (b) Mn 3s region.

Figure 4. SEM (left) and HRTEM (right) representative images of (a,b) KMn4, (c,d) KMn8, and (e,f) HKMn.

Figure 5. (a) Charge–discharge profiles at 30 mA g−1 and (b) specific capacity and efficiency for KMn8, KMn4 and HKMn during 50 cycles.

Figure 6. Cyclic voltammetry curves for KMn8, KMn4, and HKMn.

Figure 7. (a) Charge–discharge profiles at 300 mA g−1 and (b) Specific capacity and efficiency for KMn8, KMn4 and HKMn during 50 cycles.

Figure 8. XRD profile “ex situ” of KMn4 after three cycles (a) discharged (b) charged (c) KMn4 profile with comparative purpose.

Figure 9. X-ray diffraction pattern “ex situ” of HKMn post-mortem.

Table 1

Crystallographic data of KMn8 and HKMn.

Phase	KMn8	HKMn
Space group	P 63/mmc	R -3m
a (Å)	2.864 (5)	2.846 (9)
c (Å)	14.274 (2)	21.751 (6)
Rp	19.3	15.3
Rwp	18.2	16.1
RB	9.1	4.7

Table 2

Binding energies (eV) for Mn 2p and Mn 3s core level components of XPS spectra of the samples.

Sample		Mn 2p			Mn 3s
	2p1/2	2p3/2	Δ(2p1/2–2p3/2)	3s(1)	3s(2)	Δ(3s(1)–3s(2))	υMn
KMn4	654.2	642.4	11.8	89.4	84.7	4.7	3.8
KMn8	654.2	642.3	11.9	89.3	84.7	4.6	3.6
HKMn	654.4	642.6	11.8	89.6	84.9	4.7	3.8

Supplementary Materials

The following are available online at https://www.mdpi.com/article/10.3390/app12031176/s1, Figure S1: (a) Thermogravimetric analysis under N₂ for all samples. (b) XRD profile of KMn8 residue, the maxima were assigned to a mixture of phases: birnessite and K₁.₃₃Mn₈O₁₆; (c) XRD profile of the HKMn residue, the maxima were indexed to K₁.₃₃Mn₈O₁₆. Table S1. Weight loss from ATG data (%) and structural formulas for birnessite-type material obtained from EDX and ATG data.

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