# [Methylhydrazinium]2PbCl4, a Two-Dimensional Perovskite with Polar and Modulated Phases

Katarzyna Fedoruk, Dawid Drozdowski, Miroslaw Maczka, Jan K Zareba, Dagmara Stefańska, Anna Gagor, Adam Sieradzki

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Katarzyna Fedoruk, Dawid Drozdowski, Miroslaw Maczka, Jan K Zareba, Dagmara Stefańska, et al.. [Methylhydrazinium]2PbCl4, a Two-Dimensional Perovskite with Polar and Modulated Phases. Inorganic Chemistry, 2022, 61 (39), pp.15520-15531. 10.1021/acs.inorgchem.2c02206 . hal-03991673

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# [Methylhydrazinium]₂PbCl₄, a Two-Dimensional Perovskite with Polar and Modulated Phases

Katarzyna Fedoruk, Dawid Drozdowski, Mirosław Maczka,* Jan K. Zareba, Dagmara Stefańska, Anna Gagor, and Adam Sieradzki*

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Cite This: *Inorg. Chem.* 2022, 61, 15520–15531

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**ABSTRACT:** Two-dimensional (2D) lead halide perovskites are a family of materials at the heart of solar cell, light-emitting diode, and photodetector technologies. This perspective leads to a number of synthetic efforts toward materials of this class, including those with prescribed polar architectures. The methylhydrazinium (MHy⁺) cation was recently presumed to have an unusual capacity to generate non-centrosymmetric perovskite phases, despite its intrinsically nonchiral structure. Here, we witness this effect once again in the case of the Ruddlesden-Popper perovskite phase of formula MHy₂PbCl₄. MHy₂PbCl₄ features three temperature-dependent crystal phases, with two first-order phase transitions at T₁ = 338.2 K (331.8 K) and T₂ = 224.0 K (205.2 K) observed in the heating (cooling) modes, respectively. Observed transitions

involve a transformation from high-temperature orthorhombic phase I, with the centrosymmetric space group *Pmmn*, through the room-temperature modulated phase II, with the average structure being isostructural to I, to the low-temperature monoclinic phase III, with non-centrosymmetric space group *P*2₁. The intermediate phase II is a rare example of a modulated structure in 2D perovskites, with *Pmmn*(00γ)s00 superspace symmetry and modulation vector **q** ≅ 0.25c*. MHy₂PbCl₄ beats the previous record of MHy₂PbBr₄ in terms of the shortest inorganic interlayer distance in 2D perovskites (8.79 Å at 350 K vs 8.66 Å at 295 K, respectively). The characteristics of phase transitions are explored with differential scanning calorimetry, dielectric, and Raman spectroscopies. The non-centrosymmetry of phase III is confirmed with second harmonic generation (SHG) measurements, and polarity is demonstrated by the pyroelectric effect. MHy₂PbCl₄ also exhibits thermochromism, with the photoluminescence (PL) color changing from purplish-blue at 80 K to bluish-green at 230 K. The demonstration of polar characteristics for one more member of the methylhydrazinium perovskites settles a debate about whether this approach can present value for the crystal engineering of acentric solids similar to that which was recently adopted by a so-called fluorine substitution effect.

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## 1. INTRODUCTION

Considering the unprecedented promise of hybrid organic–inorganic perovskites (HOIPs) for new types of solar cells¹ and other devices, it is an all-important task to have a more in-depth understanding of the connection between structure and properties in this class of compounds. Perhaps in the photovoltaic context, the most publicity has been gained so far by three-dimensional (3D) perovskites, spearheaded primarily by MAPbI₃ (MA = methylammonium).²⁻⁵ 3D perovskites feature a general formula of ABX₃, where A is an organic or alkali metal cation, B is a divalent metal cation, and X stands for halogen. If A-site cation is organic, it must be small enough to fit into the cubic metal-halide BX₃⁻ (ReO₃⁻-type) network. Essentially, only a handful of organic cations are capable of serving as guests within 3D perovskite lattices, and the title methylhydrazinium (CH₃NH₂NH₂⁺, MHy⁺) is one of them. However, there is virtually unrestricted chemical space of 2D HOIPs and low-dimensional (1D, 0D) structures since

in these topologies the steric hindrance of the coordination network does not restrict the size of organic cations anymore. This is so for 2D perovskites, which emerge as structurally more diverse alternatives to their 3D counterparts.⁶ Indeed, in addition to changes in organic, metal, and halide components, there is also an opportunity to control the number and thickness of inorganic layers.⁷⁻⁹ Critical to the functional properties are the physical implications arising from quantum effects associated with reduced dimensionality. The inorganic layers form slabs of 2D-confined quantum structures, and as a consequence, the formed quantum wells are separated by the

Received: June 26, 2022

Published: September 21, 2022

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organic barriers. The resulting complex electronic structure is sensitive to structural inputs, which can assist in controlling the dielectric and optical properties of these structures.<sup>10–14</sup> Indeed, quantum and dielectric confinement effects in 2D perovskites increase the effective band gap and the exciton binding energy compared to 3D perovskites.<sup>15</sup> For instance, the exciton binding energies increase by more than an order of magnitude from ~10 meV for 3D perovskites to typically >150 meV for conventional 2D perovskites,<sup>15–18</sup> leading to a radically improved photoluminescence quantum yield (PLQY) for layered analogues.<sup>13,19,20</sup>

It is the innumerable choices of organic components that make possible the tailoring of linear and nonlinear optical (NLO), electrical, and structural properties of perovskites. However, in some cases, simplicity, rather than complexity, yields the most intriguing results. A prime example of that is a small M**H**y⁺ cation, which in its simplistic structure is unique in that it builds up both 2D and 3D lead halides.<sup>21–26</sup> In the case of 2D perovskites such as M**H**y₂PbBr₄ and M**H**y₂PbI₄, the small size of this cation translates to a record low separation between inorganic layers (8.91 Å at 300 K and 9.36 Å at 305 K, respectively) and a very small, as for 2D perovskites, estimated exciton binding energy (99.9 and 59.2 meV, respectively).<sup>22,25</sup> Quite an interesting aspect of using the M**H**y⁺ cation for construction of perovskites is the apparent guided assembly of non-centrosymmetric perovskite phases. Indeed, the first 3D perovskite reported, with at least one unequivocally acentric phase was M**H**yPbBr₃,<sup>21</sup> soon after followed by the discovery of M**H**yPbCl₃ with two acentric crystal phases (monoclinic and orthorhombic), verified by pyrocurrent measurements and capable even for unusual temperature switching of a second-order NLO response of SHG-low–SHG-high type.<sup>23</sup> Mixed-halide analogues M**H**yPbBr₃Cl<sub>(3-x)</sub> mirror the phase behavior of the M**H**yPbCl₃ prototype in that they contain two polar crystal phases, irrespectively of Br content.<sup>24</sup> M**H**y₂PbBr₄ is ferroelectric at room temperature with orthorhombic *P*mnn*2*₁ symmetry.<sup>22</sup> Among 2D (n = 1) M**H**y⁺-perovskites, only M**H**y₂PbI₄ does not reveal polar properties;<sup>25</sup> however, it features the unique octahedral tilt system.<sup>6</sup> The ability of M**H**y⁺ to direct non-centrosymmetric structures does not work for the 2D and even low-dimensional iodides.<sup>27</sup> The same applies to other organic cations, such as benzylammonium<sup>28–30</sup> or cyclohexylammonium,<sup>31,32</sup> wherein only chloride or bromide analogues adopt polar phases. It may be possibly explained via weakening of hydrogen bonding (HB) strength with decreasing electronegativity of halides.<sup>33</sup> Thus, the N–H···I HBs are the weakest, and therefore for iodide systems the cations may adopt the most energetically favorable alignment, i.e., without inducing a resultant dipole moment. Polar structure, *Cc*, was also reported for 2D (n = 3) BA₂M**H**y₂Pb₃Br₁₀ perovskite (BA = butylammonium).<sup>26</sup> Accordingly, one sees that there is mounting evidence that the M**H**y⁺ component promotes the formation of non-centrosymmetric phases, which however requires further experimental verification. Of large comparative value would be to explore the properties of unknown halide analogues of extant methylhydrazinium perovskites, one of which is a 2D analogue of formula M**H**y₂PbCl₄. Indeed, the multitechnique investigation of structural polar, dielectric, nonlinear, and linear optical properties of all crystal phases of M**H**y₂PbCl₄ forms the content of the present contribution.

## 2. MATERIALS AND METHODS

**Synthesis.** PbCl₂ (98%, Sigma-Aldrich), methylhydrazine (98%, Sigma-Aldrich), hydrochloric acid (48 wt % in H₂O, POCH), methyl acetate (99.5%, Sigma-Aldrich), and N,N-dimethylformamide (DMF, 99.8%) were commercially available and used without further purification. In order to obtain single crystals of M**H**y₂PbCl₄, a reaction mixture containing 15 mmol of methylhydrazine neutralized with HCl (pH = 7), 5 mmol of PbCl₂, and DMF (about 12 mL) was stirred for an hour until the complete dissolution of PbCl₂. Then the solution was placed in a glass vial with the lid slightly loosened. This smaller vial was then placed in a second larger glass vial containing methyl acetate with a thoroughly sealed lid. Colorless, plate-like crystals with dimensions of up to 5 mm were harvested after 1 week, filtered from the mother liquid, and dried at RT. A good match of their powder XRD pattern with the calculated one based on the single-crystal data (Figure S1) confirmed the phase purity of the bulk sample. Caution! Methylhydrazine is toxic and must be handled with extreme caution and the appropriate protective gear.

**Differential Scanning Calorimetry (DSC).** Heat capacity was measured using a Mettler Toledo DSC-1 calorimeter with a high resolution of 0.4 µW. Nitrogen was used as a purging gas, and the heating and cooling rate was 5 K min⁻¹. The mass of the measured sample was 26.88 mg. The excess heat capacity associated with the PT was calculated by subtracting from the data a baseline representing the system variation in the absence of the PTs.

**Single-Crystal X-ray Diffraction (SCXRD).** SCXRD experiments were carried out using an Xcalibur four-circle diffractometer (Oxford Diffraction) with an Atlas CCD detector and graphite-monochromated Mo Kα radiation. Absorption was corrected by multiscan methods using CrysAlis PRO 1.171.41.93a (Rigaku Oxford Diffraction, 2020). Empirical absorption correction using spherical harmonics, implemented in the SCALE3 ABSPACK scaling algorithm, was applied. For all structures, H atom parameters were constrained. The crystal structures of phases I and III, and the average structure of phase II were solved in Olex2 1.5³⁴ using SHELXT.<sup>35</sup> Phases I and III were refined with SHELXL.<sup>36</sup> Refinement of modulated phase II was performed using *Jana2020*.<sup>37</sup> Experimental and refinement details for all phases are summarized in Table S1. Refinement of I (*P*mmn with *a* = 5.7902(1), *b* = 17.5814(6), *c* = 5.8657(1) Å, *V* = 597.13(3) Å³, and *Z* = 2) converged to refinement factors *R*₁ = 0.02, *wR*₂ = 0.04, and *S* = 1.13. Phase III (*P*₂₁ with *a* = 11.6588(5), *b* = 17.0423(6), *c* = 12.7453(6) Å, *β* = 114.16(1)°, *V* = 2310.65(6) Å³ and *Z* = 8) was treated as a two-domain twin. Refinement converged to *R*₁ = 0.06, *wR*₂ = 0.17, and *S* = 1.02.

The refinement of modulated phase II requires a broader comment. As the satellite reflections appear along *c*\* in ca. one-fourth of the distance between the main reflections (Figure S2), one may treat this phase as a supercell of I with a four-fold multiplication of the *c* parameter. However, systematic absences of satellite peaks do not meet the extinction rules known for 3D space groups. Therefore, the (3 + 1) superspace approach was applied. The studied structure was refined in the *P*mmn(00*γ*)s00 superspace group with modulation vector **q** ≅ 0.25*cc*\* (Figure S3).<sup>38</sup> The refinement of the modulation waves started with the inorganic part. Based on Fourier maps (Figure S4), all of the Pb and Cl atoms were modulated with the assumption of a positional modulation using first-order harmonics. Later, the same approach was applied to the C1 and the terminal N2 atom of M**H**y⁺, as derived from Fourier maps for M**H**y⁺ (Figure S5). All of the positional modulation waves were treated as one-dimensional, i.e., propagating along the *a* direction. In the case of the N1 atom, a more accurate refinement was obtained when the occupational modulation was adopted. The occupancy of N1 was modulated with a crenel function with Δ*x*₄ = 0.5, and the positional modulation functions were described as harmonics in the interval (0,1). Finally, hydrogen atoms were inserted from geometry and refined as riding atoms with *U*<sub>iso</sub> = 1.2*U*<sub>iso</sub> of the maternal atom. The final *R* factors are *R*₁ = 0.02 (0.09) and *wR*₂ = 0.03 (0.12) for main reflections (satellites). The displacement of independent Pb and Cl atoms along the *a* direction as a function of the phase of the modulation *t* is shown in Figure S6a.
Cl2 demonstrates the highest displacement amplitude of ~0.20, which is greater than for Cl3 (~0.15) and for both Pb1 and Cl1 (~0.07). These displacements reveal variations of Pb–Cl bond lengths (Figure S6b) and Cl–Pb–Cl angles (Figure S6c). It is worth noting here that both from the symmetry relations and from the atomic positions of Pb and Cl atoms the 4c approximant structure of *Pcmn* symmetry is imposed for the II phase (*Pnma* in the standard setting). However, in the 4c superstructure of *Pcmn* symmetry, the amines are disordered over the *m* mirror plane, with two equally occupied positions. Thus, the conventional space group does not resolve the ordering of amines.

**Raman Studies.** Temperature-dependent Raman spectra were obtained in the 300–5 cm⁻¹ range using a Renishaw InVia Raman spectrometer equipped with a confocal DM 2500 Leica optical microscope, a thermoelectrically cooled CCD as a detector, and an eclipse filter. The excitation was performed using a diode laser operating at 830 nm, and the temperature was controlled using a Linkam cryostat cell. The spectral resolution was 2 cm⁻¹.

**Electrical Measurements.** Dielectric measurements of the examined samples were carried out using a broadband impedance Novocontrol Alpha analyzer. Electric field-dependent polarization measurements were performed on a single-crystal sample of size 0.4 × 1 × 1 mm³. The silver paste was used to ensure good electrical contact. A sinusoidal voltage with an amplitude of 1 V and a frequency in the range of 1 Hz to 1 MHz was applied across the sample. The studies were performed at quasi-static conditions in the temperature range of 150–360 K. The temperature was stabilized using nitrogen gas using the Novocontrol Quattro system. A pyrocurrent measurement was made on a single crystal with silver electrical contact. The crystal was cooled down to 150 K. During cooling, an electric poling field of 200 V/mm was applied. At 150 K, the sample electrodes were shorted for 10 min. Current measurements were performed using a Keithley 6514 electrometer during the heating of the sample from 150 to 300 K with a heating rate of 2 K/min. An aixACCT instrument was used to study the electric field-dependent electric polarization. A periodic triangular signal was used for the measurements. A high voltage was obtained using a Trek 609E6 voltage amplifier. Measurement of the polarization vs field (P–E) was carried out with a Precision Premier II Ferroelectric tester. The electrodes of conductive silver paste were placed on a single crystal with an area of 0.0226 cm² and a thickness of 345 µm. The measurement was made at a temperature of 180 K. The cooling gas was nitrogen. A maximum voltage of 500 V and frequency of 10² Hz were applied across the sample, and the data were recorded with the Virtual software.

**SHG Studies.** Temperature-resolved SHG studies and Kurtz-Perry powder test were performed using a laser system employing a wavelength-tunable Topaz Prime Vis-NIR optical parametric amplifier (OPA) pumped by a Coherent Astrella Ti:sapphire regenerative amplifier providing femtosecond laser pulses (800 nm, 75 fs) at a 1 kHz repetition rate. The output of OPA was set to 1300 nm and was used unfocused. The laser fluence at samples was equal to 0.17 mJ/cm². The single crystals of MHy₂PbCl₄ were crushed with a spatula and sieved through an Aldrich mini-sieve set, collecting a microcrystal size fraction of 125–177 µm. Next, size-graded samples were fixed in between microscope glass slides to form tightly packed layers, sealed, and mounted to the horizontally aligned sample holder. No refractive index matching oil was used. The employed measurement setup operates in the reflection mode. Specifically, the laser beam delivered from OPA was directed onto the sample at 45 deg to its surface. Emission collecting optics consisted of a Ø25.0 mm plano-convex lens of focal length 25.4 mm mounted to the 400 µm 0.22 NA glass optical fiber and was placed along the normal to the sample surface. The distance between the collection lens and the sample was equal to 30 mm. The spectra of the NLO responses were recorded by an Ocean Optics Flame T fiber-coupled CCD spectrograph with a 200 µm entrance slit. Scattered pumping radiation was suppressed with the use of a Thorlabs 750 nm short-pass dielectric filter (FESH0750). Temperature control of the sample was performed using a Linkam LTS420 heating/freezing stage. Temperature stability was equal to 0.1 K. A Kurtz–Perry test was performed by comparing the integral SHG

intensity of MHy₂PbCl₄ (measured at 160 K) to that of potassium dihydrogen phosphate (KDP) of the same particle size distribution. The same optical setup and laser beam parameters were employed for temperature-resolved studies.

**One-Photon Absorption and Photoluminescence Studies.**

The RT absorption spectrum of the powdered sample was measured using a Varian Cary 5E UV–vis–NIR spectrophotometer. Emission spectra at various temperatures under 266 nm excitation provided by a diode laser were measured with the Hamamatsu photonic multichannel analyzer PMA-12 equipped with a BT-CCD linear image sensor. The temperature of the single-crystal sample was controlled using a Linkam THMS 600 heating/freezing stage. To record decay times, a femtosecond laser (Coherent Model Libra) was used as an excitation source.

### 3. RESULTS AND DISCUSSION

DSC. The performed calorimetric scans showed two reversible PTs at $T_1$ = 338.2 K (331.8 K) and $T_2$ = 224.0 K (205.2 K) visible in the heating (cooling) mode (Figure 1 and

<figure><img src="image_10.png" /><figcaption>**Figure 1.** Changes in (a) $C_p$ and (b) S related to the PT in the heating (red) and cooling (blue) runs.</figcaption></figure>

Figure S7). The symmetrical, strong peaks seen in $\Delta C_p$ plotted as a function of temperature, in combination with the thermal hysteresis between heating and cooling cycles, indicate the first-order type of PTs. This is also confirmed by the accompanying discontinuous change in the entropy ($\Delta S$) (see inset in Figure 1b). The changes of entropy ($\Delta S$) were estimated to be 0.38 J mol⁻¹ K⁻¹ (0.82 J mol⁻¹ K⁻¹) for the PT at $T_1$ and 4.56 J mol⁻¹ K⁻¹ (3.33 J mol⁻¹ K⁻¹) for the PT at $T_2$ in the heating (cooling) mode, respectively. The symmetry reduction during the transition from HT to modulated phase results in moderate entropy changes. A significantly higher value of $\Delta S$ at the second PT is associated with symmetry breaking from modulated orthorhombic to monoclinic (see SCXRD studies). Furthermore, the overall change of $\Delta S$ in MHy₂PbCl₄ is much greater than that reported recently for the MHy₂PbI₄ (~2.88 J mol⁻¹ K⁻¹) and MHy₂PbBr₄ (~1.66 J mol⁻¹ K⁻¹) analogues.²²,²⁵ Because this material undergoes a first-order PT, its pressure dependence can be calculated using the indirect Clausius–Clapeyron method and the equation:

$$ \frac{dT_2}{dp} = \frac{2\left(\frac{\Delta V}{V}\right)}{\Delta H_{\text{molar}}} V_{\text{molar}}, \text{ where } T_2 \text{ is the PT temperature, } \Delta H_{\text{molar}} (\sim 1046 \text{ J mol}^{-1}) \text{ represents the change in the molar enthalpy, estimated from calorimetric studies, } \Delta V/V (\sim 1.8 \times 10^{-2}) \text{ is the relative volume change at } T_2, \text{ and } V_{\text{molar}} (\sim 1.75 \times 10^{-4} \text{ m}^3) $$
<figure><img src="image_11.png" /><figcaption>**Figure 2.** Details of the MHy₂PbCl₄ crystal structure in subsequent phases. (a) HT phase I, (b) 4-fold approximant of the modulated phase II, and (c) LT phase III. (d) Comparison of the atomic alignment in II and III along the [010] direction. The green and red arrows in (a, c) represent locations of the MHy⁺ dipoles.</figcaption></figure>

mol⁻¹) is the molar unit cell volume (structural data were taken from X-ray diffraction results described below). From the obtained data, the following pressure dependence of T₂ was calculated: $\frac{dT_2}{dp} = 64.7 \pm 0.3$ K kbar⁻¹. The obtained results prove that this compound is an interesting material sensitive to both pressure and temperature changes. The obtained value is one order of magnitude higher than that for [(CH₃CH₂CH₂)₄N][Mn(N(CN)₂)₃]³⁹ and two orders of magnitude higher than those for (NH₄)MF₃ perovskites (M = Mn, Co, Cd, Mg, and Zn).⁴⁰

**Single-Crystal X-ray Diffraction.** MHy₂PbCl₄ adopts three temperature-controlled crystal phases. High-temperature (HT) phase I possesses the orthorhombic, centrosymmetric *Pmmn* space group. RT phase II adopts averaged structure isostructural to I; however, as derived from the diffraction

pattern (Figure S3), it is a modulated structure with *Pmmn*(00γ)s00 superspace symmetry and vector **q** ≅ 0.25c*.³⁸ Low-temperature (LT) phase III is monoclinic with *P2*₁ symmetry. Given that this phase is polar, the second-order NLO effects can be expected, e.g., SHG (vide infra).

HT phase I is isostructural to the previously reported HT phases of the MHy₂PbI₄ and MHy₃PbBr₄ 2D analogues.²²,²⁵ The motif of I (Figure 2a) is composed of the corner-sharing [PbCl₆]⁴⁻ octahedra forming (010) layers, separated by MHy⁺ cations, which protrude out of the *m* mirror plane. Hence, the N1 atom is split into two equivalent positions with equal probability. The distance between the octahedra layers is equal to 8.79 Å.

The PbI coordination sphere consists of the Cl1 and Cl2 atoms (bridging along the *a* and *c* directions, respectively), and
<table><caption>Table 1. Distortion Parameters of the MHy₂PbCl₄ Perovskite in the Subsequent Polymorphic Phases</caption><thead><tr><th>phase</th><th><i>T</i> (K)</th><th>Pb–Cl–Pb direction</th><th>∠Pb–Cl–Pb (deg)</th><th>a.d. (deg)</th><th><i>D</i><sub>out</sub> (deg)</th><th>max<sup>a</sup> Δ<sub>d</sub> × 10<sup>−3</sup></th><th>max<sup>a</sup> σ<sup>2</sup> (deg<sup>2</sup>)</th></tr></thead><tbody><tr><td rowspan="2">I</td><td rowspan="2">350</td><td>[100]</td><td>168.27(1)</td><td>11.7</td><td>0</td><td>1.6</td><td>14.4</td></tr><tr><td>[001]</td><td>180</td><td>0</td><td>0</td><td></td><td></td></tr><tr><td rowspan="2">II<sup>b</sup></td><td rowspan="2">295</td><td>[100]</td><td>165.78(1)</td><td>14.2</td><td>0</td><td>1.7</td><td>24.7</td></tr><tr><td>[001]</td><td>172.34(1)</td><td>7.7</td><td>0</td><td></td><td></td></tr><tr><td rowspan="2">III</td><td rowspan="2">120</td><td>[100]</td><td>166.1(5)</td><td>13.9</td><td>6.1</td><td>3.4</td><td>61.4</td></tr><tr><td>[001]<sup>c</sup></td><td>160.9(5)</td><td>2.1</td><td>19.1</td><td></td><td></td></tr></tbody></table>

<sup>a</sup>Maximum distortion parameters are provided due to the existence of four inequivalent [PbCl₆]⁴⁻ octahedra in phase III. <sup>b</sup>Distortion parameters are given for modulated phase II. <sup>c</sup>The direction maintained from the axis setting of phases I and II. a.d. = 180° - ∠Pb-Cl-Pb along [100] and [001] directions; D<sub>out</sub> = 180° - ∠Pb-Cl-Pb along [010]; Δ<sub>d</sub> - bond length distortion; σ² - octahedral angle variance.<sup>41</sup>

the apical Cl3 atom. The individual octahedron is of C<sub>2v</sub> symmetry with mm2 site symmetry for Pb1, Cl1, and Cl3, and m.. for Cl2. Pb-Cl distances vary from 2.74 to 3.12 Å. The difference between the longest and shortest Pb-Cl distances (0.38 Å) is relatively higher than the ones reported for the Br- and I- analogues (0.02 and 0.14 Å for the HT phases of MHy₂PbI₄ and MHy₂PbBr₄, respectively),<sup>22,25</sup> pointing to the higher octahedral distortion in the structure described herein. Indeed, both the bond length distortion (Δ<sub>d</sub>) and octahedral angle variance (σ²) values (Table 1) are 1.6 × 10⁻³ and 14.4°², which is greater than for MHy₂PbI₄ (6.8 × 10⁻⁶ and 5.6°²) and MHy₂PbBr₄ (2.1 × 10⁻⁴ and 11.3°²).<sup>22,25</sup> This distortion results in a decrease of the Pb-Cl-Pb angle along the [100] direction, and its value defined as Def = 180° - ∠Pb-Cl-Pb is the highest (a.d. = 11.7°) among the MHy₂PbX₄ (X = Cl, Br, I) perovskites (where a.d. = 9.3° and 10.7° for I and Br, respectively).<sup>22,25</sup> Observation of the octahedra distortion is strictly connected with intermolecular interactions between the perovskite layers and MHy⁺ cations. However, the interlayer MHy⁺ cation alignment in 2D perovskites diminishes the strength of these interactions when compared to their 3D counterparts. It is noticeable, for instance, in max. σ² values -301°² (314°²) for MHyPbBr₃ (MHyPbCl₃).<sup>23,24</sup> Despite relatively weak intermolecular forces, several N-H···Cl hydrogen bonds (HBs) are formed with both N atoms as donors and the Cl1 and Cl3 atoms as acceptors (Table S2).

Lowering the temperature induces I → II PT. The effect of the unit-cell contraction as the temperature decreases leads to the reduction of the interlayer distance to approximately 8.66 Å. While the average structure of II is isostructural to I, satellite diffraction peaks along the c* direction appear in the diffraction pattern (Figure S2). As derived from the systematic absences (see caption to Figure S3), the (3 + 1)-dimensional superspace group of II is Pmmn(00γ)s00 with the modulation vector **q** ≅ 0.25c*. The 4-fold approximant of II is presented in Figure 2b. As compared to I, the atoms of the inorganic part slightly lean out of the mirror plane toward the [100] direction (Figure S8). This behavior brings consequences to the distortions of the perovskite layers. To start with, the change of the Pb-Cl-Pb angle along [001] appears with a.d. = 7.7°. Simultaneously, the maximum a.d. alongside [100] increases to 14.2°. Additionally, both Δ<sub>d</sub> and σ² values increase to 1.73 × 10⁻³ and 24.7°², respectively (Table 1, Figure S9a,b). In the case of the organic part, the MHy⁺ cation in II is ordered, and its distribution in the structure is governed by the additional translation component of the superspace group (intrinsic phase shift of 1/2) associated with the 2-fold axis (lower part of Figure 2b). This new configuration of amines is associated with the appearance of N-H···N and N-H···Cl HBs. However, the juxtaposition of distances between N atoms of neighboring

MHy⁺ as a function of the phase of the modulation *t* (Figure S9c) indicates that in II there are NH₂ groups that are not involved in hydrogen bonding. There is no N-H···Cl or N-H···N stable HBs network along the [001] direction (Figure S10a).

With further temperature lowering, the shrinking of interatomic distances strengthens the interactions between inorganic and organic constituents and eventually leads to the formation of a new phase with a stable configuration of HBs. Indeed, such a phase appears at 205.2 K (224.0 K) on cooling (heating). The LT phase III is monoclinic with a P2₁ polar space group and β = 114.16(1)° with an asymmetric unit consisting of 4 lead cations, 16 chloride anions, and 8 ordered MHy⁺ cations (Figure S11). The main details of III are shown in Figure 2c and compared to modulated phase II in Figure 2d. Unlike the HT and RT phases, in III, certain MHy⁺ cations are spontaneously rotated. From the viewpoint of polar characteristics, MHy⁺ dipoles are no longer compensated. Instead, spontaneous polarization along the [010] direction occurs. Furthermore, due to the reduced interlayer gap of 8.52(13) Å, numerous HBs are formed (Table S3). One may distinguish two kinds of HBs. The first kind is N-H···Cl with N atoms acting as donors and Cl atoms (mainly apical) as acceptors. Contrarily to II, these HBs create the network alongside both directions of propagation of the octahedra (Figure S10b). The second kind of HBs is N-H···N, where both N atoms may serve as donors and acceptors for the hydrogen atoms. As the II → III PT is associated with symmetry reduction, all atoms in the unit cell adopt a general C₁ site. The synergistic effect of strengthened intermolecular interactions and the symmetry reduction remarkably influences the shape of the perovskite layers. Besides the in-plane Pb-Cl-Pb angle deformation (max. a.d. = 13.9°), the out-of-plane octahedra tilting is observed with the D<sub>out</sub> value of 19.1°. At the same time, the octahedra distortion parameters significantly increase (Δ<sub>d</sub> = 3.4 × 10⁻³ and σ² = 61.4°², Table 1). Lastly, the II → III PT provokes a step change in lattice parameters (Figure S12a) and an enlargement of a unit cell volume (Figure S12b).

In this paragraph, a wider comment is provided on the interlayer distances in the reported compound. As indicated above, the gap between perovskite layers decreases in the order I → II → III (8.79, 8.66, and 8.52 Å, respectively). It is worth noting that such small values were not recorded before in the 2D lead chloride perovskites with [PbCl₆]⁴⁻ monolayers (Table S4). At the same time, MHy⁺ is the smallest organic cation among the listed ones. This observation agrees with the hypothesis provided in our previous paper concerning the MHy₂PbBr₄ analogue,<sup>21</sup> that the MHy⁺ cation is a key component developing 2D hybrid perovskites with a record-breaking low layer separation.
**Raman Studies.** In order to obtain further insight into the mechanism of the PTs and lattice dynamics, temperature-dependent Raman studies were performed on MHy~2~PbCl~4~ single crystals in the low-wavenumber range of 300–5 cm~−1~ (Figure 3). The observed Raman modes are tabulated in Table S5.

<figure><img src="image_12.png" /><figcaption>**Figure 3.** Temperature-dependent Raman spectra of MHy~2~PbCl~4~ crystals in a heating run for (a) x(yy + yz)x and (b) x(zz + yz)x polarization. Red, green, and blue colors correspond to the *Pmnm* phase I, modulated phase II, and *P2*₁ phase III, respectively.</figcaption></figure>

S5. According to previous studies of layered perovskites, PEA~2~PbBr~4~ and BA~2~PbBr~4~ (PEA = phenylethylammonium; BA = butylammonium) Raman spectra in the low-wavenumber range consist of five ranges. The lowest wavenumber narrow bands, which do not exhibit any splitting at LT, correspond to the octahedra rocking/twisting that could be alternatively assigned to PbBr~6~ librational modes.⁴² These modes were observed at near 27 and 22 cm⁻¹ for PEA~2~PbBr~4~ and BA~2~PbBr~4~, respectively.⁴² Raman spectra of MHy~2~PbCl~4~ show such narrow modes at 24 and 29 cm⁻¹ (values at 80 K, Table S5). The corresponding modes of MHy~2~PbBr~4~ and MHy~2~PbI~4~ were observed at 23 and 17 cm⁻¹, respectively.²⁵,⁴³ As can be seen, these modes shift weakly to higher wavenumbers with the decreasing size of the halide anion. The most intense Raman bands (weak bands), observed for PEA~2~PbBr~4~ and BA~2~PbBr~4~ in the 80–35 cm⁻¹ range (140–83 cm⁻¹ range), were attributed to Pb–Br bond bending modes (Pb–Br bond stretching modes).²⁵ These broad bands at RT

exhibited splitting into many components at LT.²⁵ For the HT phase of MHy~2~PbCl~4~, Pb–Cl bending and stretching modes are located in the 105–54 and 186–164 cm⁻¹, respectively (Table S5). It is worth noting that these bands exhibit a very pronounced shift to lower wavenumbers with the increasing size of the halide anions, i.e., to 47–45 and 137–116 cm⁻¹ for MHy~2~PbBr~4~ and 34–27 and 120–97 cm⁻¹ for MHy~2~PbI~4~.²⁵,⁴³

According to the X-ray diffraction studies, MHy⁺ cations are disordered in phase I and ordered in phase II. One would expect, therefore, to observe a significant narrowing of bands at the PT temperature. As can be noticed, Raman bands exhibit a rather weak narrowing at *T*₁ (see Figure 3). Interestingly, very similar behavior was also reported for MHy~2~PbBr~4~.⁴³ Thus, in both analogues, the dynamics of MHy⁺ cations does not exhibit a sudden change at the PT temperature. Nevertheless, the PT leads to some changes in the intensity of Raman modes. For instance, a new L(PbCl~6~) band appears at 16 cm⁻¹, and in the x(zz+yz)x polarization intensity of the 54 cm⁻¹ band drastically decreases (Figure 3). However, the observed changes at *T*₁ are weak, providing a spectroscopic argument for the significant crystallographic similarity of phases I and II.

On further lowering of temperature, lattice modes exhibit very pronounced changes when the temperature decreases from 225 to 220 K (Figure 3). First, Raman modes exhibit significant shifts and split into many components. Second, Raman bands decrease fwhm, and they become very narrow at 80 K. All of these changes point to further slowing down of the MHy⁺ cation dynamics and a significant decrease in crystal symmetry, associated with the change of distortion of PbCl~6~ octahedra and appearance of out-of-plane tilting. Note that the number of Raman bands observed at 80 K is much larger for MHy~2~PbCl~4~ (24 in the x(zz+yz)x polarization), compared to MHy~2~PbBr~4~ (nine bands).⁴¹ This observation gives strong evidence that the crystal structure of the lowest temperature phase of MHy~2~PbCl~4~ features significantly lower symmetry than the crystal structure of its bromide analogue. This conclusion is consistent with X-ray diffraction data that revealed *Pmn*2*1* and *P*2*1* symmetry for the lowest temperature phases of MHy~2~PbBr~4~ and MHy~2~PbCl~4~, respectively.

**Electrical Measurements.** A broadband dielectric spectroscopy measurement was carried out to investigate the dipolar relaxation arising from the reorientation motions of molecular dipoles and conduction arising from the translational motions of electric charges (ions, electrons). Temperature-dependent complex dielectric permittivity ε* (ε* = ε' − iε", where ε' is the dielectric permittivity, and ε" is the dielectric loss, respectively) is presented in Figure 4a,b. A slight, step-like anomaly of ε' can be observed at ~224 K on heating, related to the structural PT from phase II to phase III. However, above the observed PT, frequency dispersion can be noticed for ε*, which is probably associated with ionic/ electrical conductivity processes. To reduce the contribution of the conductivity component at higher temperatures, the modulus representation (M* = 1/ε*) was used (Figure 4c,d).⁴⁴ The bell-shaped spectra of M" and the step-like curves of M' shift toward HTs with increasing frequency, which implies the presence of conduction and dielectric relaxation processes. The visible decrease in the value of the M" coincides with the temperature of the PT from phase I to phase II. In order to investigate this behavior, the dependence of ε* and M* as a function of frequency in the temperature range of 140–360 K was performed (Figure S13). The visible bell-shaped spectra of M" allow the activation energy to be
<figure><img src="image_13.png" /><figcaption>Figure 4. Temperature dependence of the (a) dielectric permittivity, (b) dielectric loss, (c) real M', and (d) imaginary M'' components of electric modulus spectra as a function of the temperature of the MHy₂PbCl₄ single crystal along the [010] direction measured on heating. The representative curves are plotted in frequency decades between 1 Hz and 1 MHz. Dashed lines correspond to the structural PT temperatures. The changes in dielectric permittivity for the area near the PT are presented in the inset in a.</figcaption></figure>

determined. The data were parametrized in the vicinity of the peak maximum with the use of the single Havriliak–Negami function. It was noticed that in the studied temperature range, the relaxation times (τ) exhibit linear tendencies as a function of the inverse temperature (1000/T). Therefore, the relaxation times can be modeled using the Arrhenius relation:

$$ \tau = \tau_0 \exp\left(\frac{E_a}{k_B T}\right) $$

where τ₀, k_B, and E_a are relaxation times at the high temperature limit, Boltzmann constant, and activation energy, respectively. Based on this estimation, the E_a in phase I is 1.8 eV and in phase II is 0.7 eV (Figure S14). Taking into account the X-ray diffraction data, the mechanism of the observed dielectric relaxation process in MHy₂PbCl₄ can be related to the new configuration of MHy⁺ and/or ionic conductivity. The obtained values of E_a are slightly higher than those reported for related compounds such as [triethylpropylammonium]PbI₃ (0.66 eV in the HT phase and 1.09 eV in the LT phase),⁴⁵ MHy₂PbI₄ (0.48, 0.80, and 0.70 eV from the HT phase to the LT phase, respectively).²⁵

The temperature-dependent pyrocurrent of the MHy₂PbCl₄ single crystal measured along the [010] direction is presented in Figure 5. We observe a sudden increase in the value of the pyrocurrent during the heating of the sample at the PT temperature of about 224 K, confirming the material's polar properties. Despite repeated trials, we could not obtain a P–E hysteresis loop for MHy₂PbCl₄, which indicates that it is a pyroelectric material. A similar case was observed for the related 3D compound MHyPbCl₃.²³

**Temperature-Resolved SHG Studies.** Despite the fact that 2D HOIPs have been around for some time, their diverse

<figure><img src="image_14.png" /><figcaption>Figure 5. Temperature dependence of the pyroelectric current of a single crystal after poling in the DC electric field. Inset shows measured polarization as a function of the applied electric field at a temperature of 180 K.</figcaption></figure>

NLO properties have gained significant interest only in the past few years. As is the case with the majority of the 2D materials, the NLO properties of 2D HOIPs are associated with their quantum-well structure; it is influenced by the quantum and dielectric confinement introduced by inorganic and organic layers, respectively.⁴⁶ Such systems typically possess strong two- and multiphoton excited PL due to large nonlinear absorption cross sections and luminescence quantum yields.⁴⁷ This is broadly true for the majority of 2D perovskites, particularly those comprising bromine, iodine, or a mixture of those at the so-called X-site.⁴⁸ The SHG phenomenon can also
benefit from confinement effects but, on the other hand, has a strict non-centrosymmetry requirement imposed by the $\chi^{(2)}$ tensor, making this process possible only in acentric crystalline materials. For this reason, the SHG-active 2D HOIPs are not really common; the most notable examples include Rudlesden-Popper phases such as $(PEA)_2(MA)_{n-1}Pb_nI_{3n+1}$ (PEA = phenylethylammonium),⁴⁹ $(BA)_2PbCl_4$ (BA = benzylammonium)⁵⁰ $(CH_3(CH_2)_3NH_3)_2(CH_3NH_3)_{n-1}Pb_nI_{3n+1}$ ($n = 1, 2, 3, 4, \infty$)⁹ as well as $MHy_2PbBr_4$,²² a bromine analogue of the title compound. For this reason, we set out to investigate SHG properties of all crystal phases of $MHy_2PbCl_4$, in particular, to check how they compare to those of $MHy_2PbBr_4$.

A temperature-resolved SHG study of $MHy_2PbCl_4$ was performed with the use of 1300 nm femtosecond laser pumping; this wavelength was chosen to enable comparisons with extant methylhydrazinum-based perovskites. First, we will discuss TR-SHG results for the RT phase II and LT phase III. Figure 6 presents integral areas of SHG signals ($\lambda_{SHG} = 650$

<figure><img src="image_15.png" /><figcaption>Figure 6. Plots of integral intensities of the SHG signal of $MHy_2PbCl_4$ for heating (red circles) and cooling (blue circles) runs.</figcaption></figure>

nm) plotted as a function of temperature for heating (148–268 K) and cooling run (268–148 K), while experimental spectra of NLO responses are displayed in Figure S15. These data show that $MHy_2PbCl_4$ is clearly SHG-active in its LT phase III, while PT to phase II (at ca. 223 K upon heating) results in a complete loss of SHG activity. Upon cooling at ca. 193 K, SHG starts to be restored due to a return to the non-centrosymmetric phase III. PT between phases II and III is therefore reversible, as well as features broad hysteresis, which confirms its first-order character. At this point, it should be noted that the LT phase III of $MHy_2PbBr_4$ is also non-centrosymmetric.²²

In a separate experiment, we checked whether the HT phase I is SHG-active. To this end, we performed a temperature scan (300–355 K) using the same irradiation conditions and registered spectra of nonlinear emissions. As seen in Figure S16, spectra in this temperature range do not show any contribution of SHG at 650 nm, but only a third-harmonic generation (THG) signal at 433 nm, which is present for each phase regardless of its symmetry (compare with Figure S15). Accordingly, the centrosymmetric character of phase I, inferred from crystallographic data, is confirmed by these results.

In order to estimate the efficiency of the generation of the second harmonic of radiation by phase III, we performed the

Kurtz-Perry powder test in which we compared the SHG emission of $MHy_2PbCl_4$ cooled down to 160 K with that of KDP of the same particle size, but measured at RT. It turns out that the relative efficiency of SHG is about 0.21 times that of KDP at 1300 nm. This value is two times higher than that found for $MHy_2PbBr_4$.²²

From the viewpoint of NLO properties, the title compound is similar to its bromine analogue, $MHy_2PbBr_4$. The fundamental common feature is that both analogues possess three temperature-dependent crystal phases, among which only the LT phase III is SHG-active. In fact, in the case of $MHy_2PbCl_4$, the THG is present in addition to SHG. By contrast, phase III of $MHy_2PbBr_4$ showed multiphoton-excited luminescence of mixed 3- and 4-photon absorption origin in addition to SHG and THG emissions. This difference can be ascribed to the wide optical bandgap of $MHy_2PbCl_4$ (3.75 eV, see optical properties section) which effectively shifts nonlinear absorption resonances to shorter wavelengths.

All in all, the collected results demonstrate one more example of HOIP that contains $MHy^+$ cation and whose at least one crystal phase is SHG-active (acentric). While $MHy_2PbCl_4$ in its crystal architecture and phase behavior mirrors the $MHy_2PbBr_4$ analogue in many respects, it should be pointed out that $MHy$-containing 3D perovskites, $MHyPbCl_3$, $MHyPbBr_3$, and halide-mixed $MHyPbBr_3Cl_{(3-x)}$ analogues, possess acentric phases as well.²¹,²³,²⁴ In fact, these materials are the only representatives of 3D perovskites that reveal clear polar order. The apparent accumulation of examples of $MHy$-containing perovskites which are non-centrosymmetric raises the question of whether the $MHy^+$ cation—a nonchiral molecule—facilitates crystallization of acentric perovskite phases. If there is indeed something to that, the $MHy^+$ component could play a similar role in materials science as recently adopted by amine fluorination,⁵¹⁻⁵⁴ and as such, could be seen as a useful tool for inducing non-centrosymmetry-driven properties, e.g., piezoelectricity or ferroelectricity.

**Photoluminescence.** The diffuse reflectance spectrum of $MHy_2PbCl_4$ shows a narrow band positioned at 344 nm (3.60 eV) (Figure S17), which can be assigned to the excitonic absorption. Based on this result, the energy band gap ($E_g$) of the investigated perovskite was calculated using the Kubelka–Munk equation:⁵⁵

$$F(R) = \frac{(1 - R)^2}{2R}$$

where R indicates reflectance. The estimated $E_g$ value of $MHy_2PbCl_4$ is 3.75 eV (Figure S18); i.e., it is significantly larger than the $E_g$ of the bromide ($MHy_2PbBr_4 \approx 3.02$ eV) and iodide ($MHy_2PbI_4 \approx 2.20$ eV) analogues.²²,²⁵ The increase of the energy band gap when larger $I^-$ are replaced by smaller $Br^-$ or $Cl^-$ ions can be attributed to the lower electronegativity of the smaller halogen atoms.²⁰ The band gap of $MHy_2PbCl_4$ is also larger than the band gap of its 3D $MHyPbCl_3$ analogue, for which $E_g = 3.4$ eV.²³ The same behavior, attributed to quantum confinement effects, was also observed for other lead halides.⁵⁶ It is worth adding that the energy band gap and the excitonic absorption of 2D lead halide perovskites with formula $A_2PbX_4$ also become larger with a decrease in the interlayer distance.²²,²⁵,²⁹,⁵⁷,⁵⁸ Thus, we showed that $MHy_2PbI_4$ and $MHy_2PbBr_4$ perovskites exhibit exceptionally small band gaps and the most red-shifted excitonic absorption among all known $A_2PbI_4$ and $A_2PbBr_4$ analogues.²²,²⁵ The same applies to
<figure><img src="image_16.png" /><figcaption>Figure 7. (a) Temperature-dependent emission spectra of MHy₂PbCl₄ measured every 10 K from 80 to 320 K, (b) the temperature dependence of band intensity (contour map), (c) the emission intensity as a function of temperature (left side) and the shift of the band center position with temperature, (d) CIE coordinates of MHy₂PbCl₄ at various temperatures.</figcaption></figure>

MHy₂PbCl₄, wherein the band gap is smaller (excitonic absorption red-shifted) than the band gaps (excitonic absorption) of A₂PbCl₄ (100) perovskites containing large alkylammonium or aromatic cations.²⁹,⁵⁹,⁶⁰

The PL spectrum recorded at 80 K presents a relatively broad band (full width at half-maximum, fwhm = 59.5 nm) centered at 387 nm and a very broad band (fwhm = 250 nm) located at 609 nm (Figure 7a). A significant fwhm and Stokes shift of the first band excludes its assignment to a free exciton (FE) recombination and suggests that it can be attributed to a bound exciton (BE) states or defects corresponding to imperfect stacking of layers (crumpled excitons, CE).²²,²⁴,²⁹,⁶¹,⁶² Previous studies of layered perovskites often revealed the presence of broad red-shifted bands, which were attributed to the self-trapped excitons (STEs) in the radiative centers.⁶³,⁶⁴ Typically, the PL attributed to STE is observed below 150 K and was reported for some other two-dimensional lead chlorides with a strongly distorted framework as well as 3D MHyPbCl₃.¹⁹,²³,⁵⁹ We assign, therefore, the broad band of MHy₂PbCl₄ near 609 nm to STEs. The emission decay times of the purplish-blue band (λem = 387 nm) and the red one (λem= 609 nm) recorded using a 266 nm line generated by the femtosecond laser are nonexponential with a time of τ₁ = 2.2

ns, τ₂ = 5.55 ns, and τ₁ = 0.69 ns; τ₂ = 3.0 ns, respectively (Figure S19).

As can be seen in Figure 7a-c, the intensity of the band located in the red region rapidly decreases on heating and becomes almost invisible above 130 K. The intensity of the purplish-blue band also decreases on heating, and this band exhibits significant broadening above 150 K. Furthermore, the position of the band maximum shows a pronounced red shift from 394 nm at 150 K to 507 nm at 210 K (Figure 7a-c). This pronounced broadening and the red shift of the PL above 150 nm can be most likely attributed to the light-induced permanent defects.

Based on temperature-dependent emission spectra, the activation energy for the thermal quenching was calculated as follows:

$$I(t) = \frac{I_o}{1 + A_e^{-E_a/k_B T}}$$

where, I₀, Eₐ, and kB denote the emission intensity at LT, the activation energy, and the Boltzmann constant, respectively. After simple modification, the equation can be rewritten as
$$ \ln\left(\frac{I_0}{I(t)} - 1\right) = \ln A - \frac{E_a}{k_B T} $$

Figure S20 presents ln(I₀/I(T) - 1) in a linear function of 1/k_B T. The activation energy for the thermal quenching of the MHy₂PbCl₄ emission equals 366 meV, which is consistent with Eₐ values reported for many other A₂PbX₄ compounds¹⁹,⁶⁵ but is significantly larger than Eₐ reported for FE PL in MHy₂PbI₄ (59.2 meV) and MHy₂PbBr₄ (99.9 meV).²²,²⁵

The natural consequence of the broadening of the emission band and changing its position with temperature is the shift of the color rendering index CIE (Figure 7d). From 80 to 160 K sample exhibits purplish-blue emission but then the chromaticity coordinates (x, y) change more significantly and the color of the emission tunes rapidly with temperature. As a consequence, the sample glows bluish-green at 230 K.

## 4. CONCLUSION

HOIPs not only engender emerging technological interest but serve as a unique platform for fundamental studies of structure-property-function relationships. There are organic building units that facilitate the formation of specific types of structures, which can be intentionally employed to increase the likelihood of the generation of desired molecular arrangements. A growing body of evidence suggests that such a structure-directing role in HOIPs may be performed by the methylhydrazinium (MHy⁺) cation in two aspects: (i) preferred formation of non-centrosymmetric perovskite phases; and (ii) self-assembly of 2D HOIPs with an unusually low separation between inorganic layers. With these working hypotheses in mind, in this work, we sought to employ MHy⁺ for the construction of a missing member of the methylhydrazinium 2D perovskites, MHy₂PbCl₄.

Indeed, crystallographic results MHy₂PbCl₄ show that LT phase III is non-centrosymmetric (P₂₁ space group), while RT phase II, featuring the modulated phase of Pmmn (00γ)s00 superspace symmetry and HT phase I (orthorhombic, Pmmn) are both centrosymmetric. The acentric setting of phase III is corroborated by SHG studies as well as by the pyroelectric effect, showing the decay of spontaneous polarization along the [010] crystallographic direction upon PT. However, polarization could not be switched by the application of an external electric field; hence, MHy₂PbCl₄ cannot be considered ferroelectric.

Structural studies also demonstrate that MHy₂PbCl₄ establishes a new record for the short distance between inorganic layers in 2D HOIPs (8.79 Å at 350 K), breaking the previous one held by a bromine analog of the formula MHy₂PbBr₄. Nevertheless, in this case, the short interlayer distance does not translate to an unusually low exciton binding energy as was noted for bromine and iodine analogs. On the contrary, the value of exciton binding energy, estimated based on the activation energy for the thermal quenching equals 366 meV and is in the range typical for 2D perovskites. Further optical studies revealed that MHy₂PbCl₄ on heating displays a marked broadening and redshift of the higher energy band, which can most likely be attributed to light-induced permanent defects. The estimated E₉ value of MHy₂PbCl₄ is 3.75 eV, which is significantly larger than those of the bromide and iodide analogues.

All in all, MHy₂PbCl₄ constitutes a plain example of MHy⁺-directed formation of a non-centrosymmetric phase in 2D perovskite combined with the structural effect of an unusually

low separation between inorganic layers. The guided formation of acentric phases by MHy⁺ resembles that observed for ferroelectric materials comprising fluorine-substituted organic ligands. MHy₂PbCl₄ features a thermally responsive lattice, as revealed by dielectric and Raman measurements. By using the Clausius–Clapeyron relation, it was demonstrated that MHy₂PbCl₄ is not only responsive to temperature, but its structure should also display strong structural responsiveness to pressure stimuli, warranting further studies of pressure-dependent physical properties.

## ■ ASSOCIATED CONTENT

### ■ Supporting Information

The Supporting Information is available free of charge at https://pubs.acs.org/doi/10.1021/acs.inorgchem.2c02206.

Figures: DSC traces, projections of crystal structures, dielectric curves, energy activation, SHG spectra, THG spectra, diffuse reflectance, emission spectra. Tables: crystallographic data, hydrogen-bond parameters for the studied compound at different temperatures, structural and optical parameters for selected A₂PbBr₄ perovskites (PDF)

Video: Modulation movie of phase II (MPG)

### ■ Accession Codes

CCDC 2164381–2164383 (for the structure of MHy₂PbCl₄ at 350 K, for the averaged structure of MHy₂PbCl₄ at 295 K, or the structure of MHy₂PbCl₄ at 120 K, respectively) contain the supplementary crystallographic data for this paper. These data can be obtained free of charge via www.ccdc.cam.ac.uk/data_request/cif, or by emailing data_request@ccdc.cam.ac.uk, or by contacting The Cambridge Crystallographic Data Centre, 12 Union Road, Cambridge CB2 1EZ, UK; fax: +44 1223 336033.

## ■ AUTHOR INFORMATION

### Corresponding Authors

Miroslaw Maczka – Institute of Low Temperature and Structure Research, Polish Academy of Sciences, 50-422 Wrocław, Poland; ● orcid.org/0000-0003-2978-1093; Email: m.maczka@intibs.pl

Adam Sieradzki – Department of Experimental Physics, Wrocław University of Science and Technology, 50-370 Wrocław, Poland; ● orcid.org/0000-0003-4136-5754; Email: adam.sieradzki@pwr.edu.pl

### Authors

Katarzyna Fedoruk – Department of Experimental Physics, Wrocław University of Science and Technology, 50-370 Wrocław, Poland; ● orcid.org/0000-0001-7485-7144

Dawid Drozdowski – Institute of Low Temperature and Structure Research, Polish Academy of Sciences, 50-422 Wrocław, Poland; ● orcid.org/0000-0001-5918-5503

Jan K. Zareba – Advanced Materials Engineering and Modeling Group, Wrocław University of Science and Technology, 50-370 Wrocław, Poland; ● orcid.org/0000-0001-6117-6876

Dagmara Stefańska – Institute of Low Temperature and Structure Research, Polish Academy of Sciences, 50-422 Wrocław, Poland; ● orcid.org/0000-0002-1051-3761

Anna Gagor – Institute of Low Temperature and Structure Research, Polish Academy of Sciences, 50-422 Wrocław, Poland
Complete contact information is available at:
https://pubs.acs.org/10.1021/acs.inorgchem.2c02206

## Notes

The authors declare no competing financial interest.

## ACKNOWLEDGMENTS

This research was supported by the National Science Center (Narodowe Centrum Nauki) in Poland under Project No. 2019/35/B/ST5/00043. J.K.Z. acknowledges support from Academia Iuvenum, Wroclaw University of Science and Technology.

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