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Article

Morphology Control of PbZrxTi1-xO3 Crystallites under Alkaline Hydrothermal Conditions

by
Marjeta Maček Kržmanc
1,*,
Zdravko Kutnjak
2 and
Matjaž Spreitzer
1
1
Advanced Materials Department, Jožef Stefan Institute, Jamova 39, 1000 Ljubljana, Slovenia
2
Department of Condensed Matter Physics, Jožef Stefan Institute, Jamova 39,1000 Ljubljana, Slovenia
*
Author to whom correspondence should be addressed.
Crystals 2022, 12(11), 1514; https://doi.org/10.3390/cryst12111514
Submission received: 28 September 2022 / Revised: 17 October 2022 / Accepted: 19 October 2022 / Published: 25 October 2022
(This article belongs to the Special Issue Advanced Electronic Ceramics)
Browse Figures
Versions Notes

Abstract

:
Outstanding ferroelectric and piezoelectric properties of PbZrxTi1-xO3 (PZT) make nano and sub-micrometer particles of this material interesting for future nanotechnological applications as well as for fundamental studies of ferroelectricity at the nanoscale. In the present work, the prospects of a new hydrothermal approach were explored to control the particle size, aggregation stage, and composition of the PZT with the target composition of Zr/Ti = 60/40 (x = 0.6). Starting with water-soluble Zr-, Ti-, and Pb-precursors, the PZT formation was examined in the broad base (KOH) concentration range. The PZT particle size and composition were governed by the ratio of KOH with respect to Pb and not by the absolute KOH concentration (cKOH). The incorporation of Zr into the PZT perovskite phase began to decline at KOH:Pb ≤ 1.7 and at KOH:Pb > 20. In the concentration range of 20 ≥ KOH:Pb > 1.5, the PZT particles adopted a cube-like shape, the size of which decreased with a decrease in the KOH:Pb ratio. The smallest (<200 nm) and well-separated PZT particles were obtained at KOH:Pb = 1.7. The prevailing PZT crystal structure at a Zr/Ti composition of around 60/40 was rhombohedral; the tetragonal phase also began to appear in Ti-richer PZT compositions (Zr/Ti ≤ 50/50). The developed understanding established the basis for further tailoring of PZT particle morphologies for application-oriented or fundamental research.

1. Introduction

Exceptional dielectric, ferroelectric, pyroelectric, and piezoelectric properties of PbZrxTi1-xO3 (PZT) have already been exploited in many practical devices such as piezoelectric transducers, microelectromechanical systems (MEMS), pyroelectric infrared detectors, and many others [1,2,3,4]. Due to such great application potential, PZT has been prepared and studied as thin films [5], sintered ceramics [6], single crystals [7], and free-standing nanoparticles [8]. PZT compositions with Zr content in the range of 0.4 < x < 0.6 have aroused the greatest scientific curiosity due to the best ferroelectric and piezoelectric properties around the morphotropic phase boundary (MPB) (Zr/Ti = 52/48 (x = 0.52)). Bulk PZT with 0 ≤ x ≤ 0.52 and with 0.52 < x ≤ 1 exhibit a tetragonal (P4mm) and rhombohedral (R3c) crystal structure, respectively [1]. PZT nano and sub-micrometer particles are foreseen for many advanced future applications in printed electronics, composites for sensors and actuators, 3D printing [4], and piezoelectric energy harvesting devices [9]. Moreover, PZT nanoparticles are also of great interest in the fundamental studies of ferroelectricity at the nanoscale and experimental demonstrations of the Hopfion and vortex topological states in ferroelectric nanoparticles [10]. Since the development of lead-free piezoelectrics has not yet reached the stage to fulfill all application-related properties (costs, mechanical and thermal properties, reproducibility, electrical conductivity, and lifetime), PZT is still allowed to be used in piezoelectric devices despite toxic environmental issues that arouse from evaporation of Pb at high calcination and sintering temperatures [11,12]. Furthermore, PZT ceramics and nanoparticles also attract great scientific attention in obtaining a general understanding of the origin of high piezoelectricity at the MPB and ferroelectricity at the nanoscale, respectively. These are the main reasons why PZT is still the subject of scientific research.
Many of above-mentioned nanotechnology applications require non-aggregated particles with a narrow size distribution and well-defined composition. The hydrothermal method has been proved as one of the most appropriate methods for preparation of various controlled morphologies of perovskites [13,14,15,16,17,18], including synthesis of PZT solid solutions.
Despite quite a few reports that dealt with the formation of PZT under hydrothermal or solvothermal conditions [2,3,4,8,19,20,21], systematic conclusions about the effect of a particular experimental parameter on the PZT morphology were difficult to infer from these studies. The determinations of systematic correlations were hindered because the syntheses were performed using various Zr- and Ti-precursors (TiCl4 and ZrCl4 [21], alkoxides [20], Ti−alkoxides and water-soluble Zr-precursor [3,8,19], etc.). In these studies, precipitation and alkali conditions in hydrothermal media were exclusively achieved by a KOH mineralizer, the concentration of which was typically expressed in mol/L without the indication of the concentration correlations between KOH and perovskite ions (Pb2+, Zr4+, Ti4+). The morphological development of PZT in a wide KOH concentration range is also yet to be systematically addressed. In the present work, we attempted to fill above-mentioned knowledge gaps in the understanding of key principles that govern the morphological development of PZT under hydrothermal conditions. In this study, the proposed hydrothermal synthesis route for formation of PZT from water-soluble ZrOCl2·8H2O and titanium(IV) bis(ammonium lactato) dihydroxide (TALH) was new and simple. The latter stemmed from the fact that no organic solvents or stabilizers were needed for preparation of the homogeneous solution of both precursors or to control their hydrolysis rates, respectively. The main goal of the work was to examine the formation of PZT in a broad KOH concentration range and to determine the optimal base concentration for formation of non-aggregated sub-100 nm PZT particles with the target PZT composition of Zr/Ti = 60/40. In the future, we would like to experimentally confirm the existence of hopfions in such particles as was predicted by Luk’yanchuk et al. [10]. The concentration of the KOH solution was expressed with respect to perovskite ions (specifically KOH:Pb) and we proved that this parameter determined the PZT morphology and not the absolute KOH concentration.
The presented systematic research identified the experimental conditions for formation of non-aggregated PZT particles with sub-200 nm particle size and composition close to MPB. Developed understanding establishes the basis for further optimization of the size and composition of the PZT particles, that can find several interesting applications and serve as model system for fundamental studies of nanoscale ferroelectricity.

2. Materials and Methods

2.1. Chemicals

The chemicals used for the syntheses of PZT crystallites were: a titanium(IV) bis(ammonium lactato) dihydroxide (TALH) water solution with a thermogravimetrically determined 55.2 wt % of the TALH precursor (Aldrich, St. Louis, MO, USA); zirconyl chloride octahydrate (ZrOCl2 · 8H2O, 98% (Acrocs Organics, Geel, Belgium); lead (II) acetate trihydrate (Pb(OOCCH3)2·3H2O, 99% (Alfa Aesar, Haverhill, MA, USA); and potassium hydroxide (KOH, ≥ 85% (Sigma-Aldrich)). Syntheses were performed using ultra-pure water (18.2 MΩ.cm; Purelab Option-Q7, ELGA).

2.2. Synthesis Procedure

The preparation of the PbZrxTi1-xO3 (PZT) crystallites with the target compositions corresponding to x = 0.6 (PZT06, Zr/Ti = 60/40), x = 0.7 (PZT07, Zr/Ti = 70/30), and x = 0.8 (PZT08, Zr/Ti = 80/20) included three major steps: (i) precipitation of initial precursors, (ii) a hydrothermal reaction, and (iii) washing of the reaction product and removal of the excessive amount of PbO·H2O with 1 M of HNO3. In all syntheses, Pb(OOCCH3)2·3H2O was applied in excess of 25% with respect to the titanium and zirconium precursors (molar ratio: Pb/(Zr + Ti) = 1.25). The amounts of added KOH are expressed as KOH:Pb molar ratios; for easier comparison with the literature data, the content of KOH is also given in mol/L (Table 1). For the target composition of x = 0.6, the initial precursors were precipitated either in one step or in two steps (with intermediate precipitation of a Ti-Zr gel). In the one-step synthesis procedure, the individual precursors were dissolved in ultra-pure water in amounts resulting in the initial concentrations presented in Table 1. The starting solutions of TALH, ZrOCl2, and KOH were prepared in glass beakers while the Pb(OOCCH3)2·3H2O was dissolved directly in the Teflon (PTFE) insert of a Parr autoclave. For the preparation of the homogeneous solution of TALH and ZrOCl2, appropriate volumes of both solutions were mixed together to provide the initial target Zr/Ti ratio. The precipitation started with the addition of the KOH solution to a water solution of lead acetate; finally, the solution of the mixed Ti-Zr precursor was also added dropwise to this alkaline suspension of white precipitate in the PTFE insert. All of the Pb-, Ti-, and Zr-precursors precipitated under these alkaline conditions. A PTFE insert containing 50 mL of alkaline suspension was closed in a stainless steel Parr autoclave (4748) that was put in preheated oven at 235 °C and kept at this temperature for 12 h and then cooled down to room temperature by natural cooling. The one-step precipitation procedure was applied for PZT at x = 0.6 and higher KOH:Pb molar ratios (3 ≤ KOH:Pb ≤ 40). To enable formation of a pure perovskite phase at KOH:Pb < 4, the Zr- and Ti-precursors were precipitated separately and the formed Ti-Zr gel was washed until reaching a neutral pH and added to the precipitated PbO·H2O before a hydrothermal reaction, which also took place at 235 °C for 12 h. This so-called two-step precipitation process was applied in the synthesis of PZT at the proposed x = 0.6, x = 0.7, and x = 0.8 and 1.5 ≤ KOH:Pb ≤ 3. In all cases, the intermediate precipitation of the Zr-Ti-precursors was conducted with an excessive amount of KOH corresponding to (KOH/(Zr + Ti)) = 7.8. The concentrations of the Pb2+, Zr4+, and Ti4+ ions that were bound in various precipitates in the precursor solutions before the hydrothermal reaction are presented in Table 1. After the hydrothermal treatment, the reaction product was firstly washed with water to remove excess alkalis and other dissolved ions. In next step, the precipitate was soaked in 1 M of HNO3 for 5 min. This short-time acid treatment did not influence the perovskite PZT phase but dissolved the excessive PbO·H2O. Then, the remains of acids were eliminated using water washing. Finally, the powder was washed with ethanol and dried in ambient conditions.

2.3. Characterization

The phase composition and crystal structure of the synthesized PZT samples were investigated via powder X-ray diffraction (XRD) measurements using a PANalytical X’Pert PRO MPD X-ray diffractometer (Almelo, the Netherlands) with CuKα1 radiation (λ = 1.5406 Å). The XRD patterns were collected in the range of 20° to 70° 2Θ in steps of 0.026° with an integration time of 500 s. The morphology and chemical compositions of the as-prepared PZT particles were examined using field-emission scanning electron microscopes (FE-SEM; JEOL JSM-7600 F and Thermo Fischer Verios 4G HP, Waltham, MA, USA) equipped with an Oxford Instruments energy-dispersive X-ray spectrometer (EDS). The particle sizes (the lengths of the cube edges) were evaluated in the SEM images with the help of Smile View software (JEOL, Tokyo, Japan). For the statistics, at least 200−300 particles were assessed to determine the average lengths of the cube edges. Elemental and chemical compositions of the PZT particles were determined with an Oxford EDS system (Ultim Max SDD 65 mm2) attached to the Thermo Fisher Verios 4G HP. PZT particles were coated with carbon (6 nm) to prevent charging and at least 7 particles of each type of the PZT sample were analyzed and the average compositions were calculated.

3. Results and Discussion

In this work, titanium(IV) bis(ammonium lactato) dihydroxide (TALH) and ZrOCl2·8H2O were deliberately selected to avoid dangerous (TiCl4 and ZrCl4) or moisture-sensitive (Ti- and Zr-alkoxides) chemicals that would complicate the synthesis procedure. Additionally, these water-soluble precursors enabled the formation of a homogeneous solution of Ti4+aq and Zr4+aq and their uniform precipitation with the addition of KOH, which in the further hydrothermal step ensured a more even dissolution of both precipitates (ZrO2·nH2O and TiO2·nH2O) and consequently enabled better control of the Zr:Ti ratio in the formed PZT perovskite phase. Similar to other ABO3-type perovskites [13,15,16,18,22] formation of PZT under hydrothermal conditions requires an alkaline pH in which dissolved Ti(OH)62− and Zr(OH)62− react with dissolved Pb2+ and form perovskite PZT under supersaturation. The existence of Ti(OH)62− and Zr(OH)62− species at an alkaline pH were predicted according to the “charge-pH” diagram reported by Livage et al. [23]. In an analogy with the equation for the formation of ABO3 perovskites under hydrothermal conditions [15,17], the PZT crystallization can be expressed by Equation (1):
Pb2+(aq) + xZr(OH)62−(aq) + (1-x)Ti(OH)62−(aq) → PbZrxTi1-xO3(s) + 3H2O
Considering that the base (KOH) was involved in the formation of above-mentioned Zr- and Ti-aqueous species and the type of lead-containing species depended on the pH [24], the ratio of KOH to Pb, Zr, and Ti was a relevant parameter, not just the molarity of the KOH. For this reason, the alkaline conditions in this work are demonstrated (discussed) as the KOH:Pb ratio. When knowing the relation between the added amounts of Pb with respect to Zr and Ti, the KOH content can at any point also be expressed as the KOH:Zr or KOH:Ti ratio. We confirmed in the contiunuation that the ratio between the KOH and perovskite ions was important in controlling the size of the PZT crystallites and not the absolute concentration of KOH. Xu et al. [8] observed a great variation in the size of PZT crystallites (from 4 nm nanoparticles to several-micrometer-sized cubes) with the change in KOH concentration from 4 mol/L to 1 mol/L, respectively. Inspired by this work, we decided to examine in greater detail the role of alkaline conditions in controlling the morphology of PZT particles. In particular, we focused on the conditions that could enable formation of sub-100 nm PZT crystallites, which might serve as the model system for experimental investigations of theoretically predicted configurations of the polarization field (Hopfions, vortex) in confined ferroelectrics.

3.1. Formation of the PZT with the Target Zr/Ti = 60/40 (PZT06) through One-Step Precipitation Approach

Based on the work of Xu et al. [8], PZT nanoparticles are expected to form at high KOH concentrations. For this reason, our research began with large base contents (KOH:Pb = 40:1, 30:1, and 20:1 (Table 1)) in which the initially added KOH was expected to be high enough for the precipitation of the precursors and also provided and alkaline pH for formation of the PZT perovskite phase under hydrothermal conditions. The SEM examination of the PZT06 samples that were synthesized at 235 °C for 12 h at KOH:Pb = 40:1 and 30:1 disclosed the formation of two types of morphologies. Both samples appeared very similar and were characterized by highly aggregated nanoparticles and micrometer-sized crystallites (Figure 1). Backscattered electron (BSE) images further indicated that the brighter micrometer-size crystallites consisted of elements with a higher atomic mass compared to those with a darker nanostructural phase. This was also confirmed by the EDS analyses, which showed that the nanoparticle aggregates were rich in Zr and K while Ti and Pb were present in smaller amounts. The attempt normalization of the EDS results to the perovskite ABO3 composition did not support the perovskite structure in the nanoparticle aggregates (Table 2).
On the contrary, the micrometer-sized crystallites were richer in Pb and Ti and their normalized EDS composition on average shows a good agreement with the perovskite structure. We believe that some deviation from the ideal perovskite composition was the consequence of the entanglement of both phases at several places (Figure 1d,e). In accordance with the accumulation of Zr in the nanoparticle aggregates, the Zr/Ti ratio in the micrometer-sized crystallites was smaller (39/68) than the target ratio of Zr/Ti = 60/40. The XRD patterns of both PZT06 samples (OH:Pb = 40:1 and 30:1) were identical and showed the formation of the tetragonal PZT phase, which could be indexed according to the P4mm space group (ICDD PDF reference code: 04-014-6916) (Figure 2). We are confident that the tetragonal XRD reflections resulted from the micrometer-sized PZT crystallites and not from nanoparticle aggregates because the composition of the latter did not correspond to the perovskite phase. Considering that apart from the XRD diffraction lines belonging to the perovskite phase, there were no other reflections, we assumed that the Zr-rich nanoparticles were most probably amorphous or nanocrystalline with very broad and low-intensity reflections that could not be discerned from the XRD pattern. The formation of the tetragonal structure of the Ti-richer PZT phase was also in accordance with the reported PZT phase diagram [1,25]. In view of the alkaline conditions, the studied PZT06 with a KOH:Pb ratio of 40:1 corresponded to similar concentrations ratios of PZTOH (0.1 mol/L) and KOH (4 mol/L) in the research of Xu et al. [8], who reported the formation of 4 nm tetragonal PZT nanoparticles. Due to disagreement of our observations with this previous report, we focused in the next step on formation of PZT at lower KOH contents. Zr- and K-rich nanoparticle aggregates nearly disappeared at KOH:Pb = 20:1, where a few large micrometer-sized cube-like crystallites became the predominant morphology. Many of these large PZT cubes were intergrown together whereby the typical cube consisted of densely packed smaller crystallites with a size of a few 100 nm (Figure 3a and Figure S1). According to the EDS analysis, Ti and Zr ions were incorporated in these perovskite crystallites in a ratio that was very close to the target Zr/Ti = 60/40 ratio (Table 2). In line with the average Zr/Ti > 50/50, the rhombohedral phase with S.G. R3c (ICDD PDF: 01-078-4666) was in addition to the tetragonal phase observed in the XRD pattern of PZT06 obtained at KOH:Pb = 20:1. The dominance of the rhombohedral over the tetragonal PZT phase became the characteristic of the PZT06 samples prepared at a KOH:Pb of 6:1, 5:1, and 4:1. Apart from the rhombohedral and tetragonal phases, a monoclinic phase also could be present at PZT compositions close to MPB [26,27]. However, for clear and accurate distinction between the phases, synchrotron powder XRD measurements are required [27]. The EDS analysis revealed that all of them on average contained Zr/Ti ≥ 50/50 and therefore their crystal structures were consistent with the reported phase diagram [1,25]. Good matching of the experimentally determined and target composition suggested that no secondary phase was formed. This was also confirmed by BSE microscopy (Figure 3d). The typical morphologies of these three PZT06 samples (KOH:Pb ⇒ 6:1, 5:1, and 4:1) were well-separated cubes, the size of which decreased from 650 nm to 410 nm for the PZT06 prepared at KOH:Pb = 6:1 and KOH:Pb = 4:1, respectively (Figure 3 and Figure 4; Table 2). Some of the cube facets were flat, but the presence of small and rather shallow holes in the middle of the facets were also quite common (Figure 3c). Similar to the large, several-micrometer-large cubes (PZT06 ⇒ KOH:Pb = 20:1), some of these submicrometer-sized cubes appeared to consist of smaller intergrown particles. The particle morphology always reflected the mechanism of growth. Formation of the PZT structures under the studied hydrothermal conditions certainly occurred through the dissolution and precipitation process. However, more detailed studies are needed to elucidate whether the growth involved the template (Pb3O4), as proposed for the hydrothermal formation of PbTiO3 platelets [28]; or oriented attachment [29], which is also often present in the growing of polar structures [16,30], as also was the case of PZT. According to the observed trend of a decrease in the PZT cubes with a decrease in the KOH:Pb ratio, further lowering of the size of the PZT particles might presumably be achieved by a further decrease in the KOH:Pb ratio (KOH:Pb < 4). Nevertheless, considering that OH− ions are a prerequisite for the precipitation of lead hydroxide (PbO·H2O), hydrous zirconia (ZrO2·nH2O), and hydrous titania (TiO2·nH2O), as well as in the formation of Ti(OH)62− and Zr(OH)62− species under hydrothermal conditions, there were several doubts regarding whether the PZT perovskite could still form at KOH:Pb < 4 when the synthesis is performed using the one-step precipitation approach. The assumption was verified for the PZT06 at KOH:Pb = 3. The SEM examination revealed a drastic change in the morphology (Figure 3e,f). Instead of cubes, much larger dendrite-like crystallites and some other irregular morphologies appeared. The length of a typical dendrite was around 1–2 μm and consisted of several intergrown crystallites (Figure S2). BSE microscopy together with an EDS analysis confirmed that the dendrite-like structures exhibited a PZT perovskite composition with Zr/Ti = 31/69 while the additional phase contained more Zr and less Pb and Ti (Table 2). In line with the titanium-richer PZT perovskite phase, this predominantly exhibited a tetragonal crystal structure, as was evident in the XRD pattern, in which some extra diffraction lines were also present at around 35° 2 Θ; these reflections could not be indexed by any known phase (Figure 2, curve f). Based on the above results, we inferred that in this low base concentration range, the incorporation of Zr into the perovskite structure required a higher pH than that of the Ti. Hence, the modification of the synthesis procedure was needed to prepare sub-100 nm PZT particles with the targeted x = 0.6 composition.

3.2. Hydrothermal Formation of PZT Using Two-Step Precipitation Approach

The strategy to decrease the PZT particle size with a decrease in the KOH content (KOH:Pb ratio) was simple and appealing and consequently deserved further attention. An additional lessening of the KOH content in the hydrothermal reactor was possible when the precipitation of constituent ions was conducted in a separate step and the excessive base is washed out from the precipitate. Starting with a pH-neutral precipitate, the amount of KOH needed to provide an alkaline pH for formation of the PZT under hydrothermal conditions could be smaller and more easily controlled. In the present research, only the Zr- and Ti-precursors were precipitated in the separate step (see Table 1 in the Section 2) but not lead acetate. Specifically, due to the amphoteric nature of PbO, different soluble Pb-containing species (e.g., Pb6O(OH)64+ or Pb(OH)3− [24]) might have formed with an increase in the added base in the precipitation process and therefore some loss of Pb may have occurred if a separate precipitation approach also was used for Pb2+ ions. The Zr4+ and Ti4+ ions were precipitated together to enable their intimate mixing in the precipitate and consequently ensure a more homogeneous dissolution (Ti(OH)62− and Zr(OH)62− formation) in the hydrothermal step and incorporation afterward of both ions in the PZT structure at a ratio that was close to the target composition.

3.2.1. Controlling of the PZT Particle Morphology Using Two-Step Precipitation Approach and Initial Zr/Ti = 60/40 (PZT06)

To study the variation in the PZT06 particle size as a function of the KOH concentration in the hydrothermal reactor, the syntheses of the previously precipitated Zr-Ti system with the initial Zr/Ti = 60/40 were performed at KOH:Pb = 3:1, 2:1, 1.7:1, and 1.5:1. In these conditions, similar to those in the one-step precipitation process, the PZT particles typically adopted a cube-like shape (Figure 5). In line with the already-observed decrease in the particle size with the lowering of the KOH content, in the two-step process, the average length of the cube edge also decreased in the synthesis performed at 3 ≥ KOH:Pb ≥ 1.7. For example, when the KOH:Pb ratio was changed from 3:1 to 1.7:1, the average PZT particle size decreased from approx. 450 nm to 172 nm (Figure 5a–c; Table 2). The conditions of KOH:Pb = 1.7:1 enabled the formation of the smallest and most non-aggregated PZT particles. Based on a quite broad particle size distribution, the size of a small fraction of the particles approached 100 nm; however, the desired sub-100 nm particles were very rare (Figure 4b and Figure 5c). A further decrease in the KOH content (OH:Pb = 1.5:1) resulted in more aggregated particles (Figure 5d), whereby the size of the typical aggregate exceeded the size of the separated particles obtained at a bit higher KOH:Pb ratio equal to 1.7:1 (Figure 5c). The EDS analysis disclosed that the average composition (PbZr0.55Ti0.43O3) of the PZT obtained at KOH:Pb = 3:1 showed the best agreement with the target PbZr0.6Ti0.4O3 composition (Table 2). However, when the synthesis was performed at KOH:Pb = 2:1, the Zr amount had already slightly decreased (PbZr0.52Ti0.48O3). Further lowering of the Zr content in the perovskite phase (Table 2) was observed at smaller KOH concentrations (KOH:Pb = 1.7:1 and 1.5:1), indicating that in this base concentration range the incorporation of the zirconium into the PZT perovskite phase required higher base concentrations than titanium. The crystal structural analysis revealed that rhombohedral phase was the prevailing phase for PZT obtained at 3 ≥ KOH:Pb ≥ 1.7 while the tetragonal phase began to appear at KOH:Pb = 1.5:1 (Figure 6). The latter agreed with the higher Ti content with respect to Zr in the perovskite phase (Table 2) as well as with the reported PZT phase diagram [1,25].
Understanding of the chemistry of the hydrothermal transformation implied that concentration of the base (KOH) with respect to the metal ions constituting the PZT was important in governing the transformation process and consequently determined the morphology of the final PZT particles. Without knowing these concentration relations, the role of KOH concentration in the PZT formation could not be well interpreted. To confirm this empirical prediction, two synthesis experiments with a double concentration of Pb, Zr, and Ti with respect to those presented in Table 1 (PZT06 (two-step), KOH:Pb = 3:1) were performed. In the first synthesis trial, the concentration of KOH was also two times higher, leading to KOH:Pb = 3:1; while in the next synthesis the absolute concentration of KOH was the same as for the usual synthesis (0.105 mol/L), resulting in KOH:Pb =1.5:1. A comparison of the morphologies (Figure S3) revealed that when KOH:Pb = 3:1, PZT cubes with a similar size formed irrespective of the double difference in the concentrations of the Pb, Zr, and Ti precursors. When the KOH concentration remained the same while the contents of Pb, Zr, and Ti were doubled, the final PZT morphology again resembled that of the usual experiment with the same KOH:Pb ratio equal to 1.5:1 and not the morphology obtained in the usual experiment with the same absolute KOH concentration. The results undoubtedly highlighted the importance of the consideration of the concentration relations between the base and perovskite ions in the designing of the PZT perovskite particles.

3.2.2. Controlling of the PZT Particle Morphology Using Two-Step Precipitation Approach and Initial Zr/Ti = 70/30 (PZT07) and Zr/Ti = 80/20 (PZT08)

In view of larger PZT particle growth at higher KOH concentrations, the increment in the KOH:Pb ratio was not the right strategy to achieve the target Zr/Ti = 60/40 composition and fulfill the requirement of small sub-100 nm PZT particles. For this reason, we attempted to enhance the incorporation of zirconium in the perovskite phase by increasing the Zr content in the precursor solution. For a better understanding of the correlations between the concentrations, morphology, crystal structure, and final compositions of the formed perovskite phase, the syntheses of the PZT particles began with the precursor solutions with higher initial Zr/Ti = 70/30 (PZT07) and Zr/Ti = 80/20 (PZT08) and were performed in hydrothermal conditions with controlled KOH contents in the range of 1.5 ≤ KOH:Pb ≤ 3. The formation of the cubes, the size of which decreased with KOH:Pb but increased with the initial Zr:Ti ratio (Figure 4) and enhanced aggregation, particularly at KOH:Pb = 1.5 (Figure 7 and Figure 8), all clearly showed that the approach of using higher initial Zr:Ti ratios was far from beneficial in the preparation of sub-100 nm PZT particles with the target Zr/Ti = 60/40. Nevertheless, the understanding of the structural and compositional development could still provide useful information that improved the comprehension of the hydrothermal PZT formation. As was evident in the EDS analysis, the Zr content in the PZT was the highest (Zr/Ti = 60/40) at KOH:Pb = 3:1 and was the same for both initial Zr/Ti ratios of 70/30 and 80/20 (Table 2). These results implied that at KOH:Pb = 3, the amount of incorporated Zr could not be enhanced by the increase in the Zr/Ti ratio in the precursor solution. Similarly, as observed for the initial Zr/Ti = 60/40, the Zr/Ti ratio in the formed perovskite phase decreased with a decrease in the KOH concentration despite higher initial Zr/Ti ratios of 70/30 and 80/20 (Table 2). The lowest Zr content was observed in the perovskite dendrites that formed from the precursors at the initial Zr/Ti = 80/20 and KOH:Pb = 1.5:1 (Figure 8d). Similar to the initial Zr/Ti = 60/40, the crystal structure was rhombohedral at OH:Pb = 3:1 and the tetragonal phase began to appear at lower KOH contents (Figures S4 and S5).
The above findings again confirmed that under these hydrothermal conditions the incorporation of zirconium into the perovskite lattice compared to titanium required a higher base concentration, which inversely led to larger particle sizes. In light of such conclusions, the formation of sub-100 nm PZT particles at Zr/Ti = 60/40 seemed to be somehow elusive in the present experimental conditions. Nevertheless, PZT particles with a size close to 100 nm and a composition of Zr/Ti = 46/54 that formed at OH:Pb = 1.7:1 from the initial Zr/Ti = 60/40 showed that with the appropriate modification of the experimental conditions, the target morphology and composition of the PZT are achievable.

4. Conclusions

The formation of PZT from water-soluble Zr-, Ti- and Pb-precursors in different alkaline (KOH) hydrothermal conditions was investigated to identify the key concentration correlations that governed the PZT particle morphology, crystal structure, and composition. We found that PZT crystallized in the target composition (Zr/Ti = 60/40) and rhombohedral structure in a limited range of concentration ratios between KOH and Pb ions. In the one-step precipitation approach, zirconium did not incorporate entirely in the PZT phase at KOH:Pb > 20 and at KOH:Pb ≤ 3. In the concentration range of 20 > KOH:Pb ≥ 4, the PZT perovskite particles adopted a cube shape, were well separated, and became smaller at lower KOH:Pb ratios. The formation of PZT at lower KOH:Pb ratios and consequently smaller PZT particle sizes was achieved via preparation of a pH-neutral Zr-Ti precipitate before the hydrothermal reaction at 235 °C for 12 h (two-step precipitation approach). Using this strategy, the PZT particle size was decreased to less than 200 nm and the particles remained well separated for KOH:Pb = 1.7; the average Zr/Ti ratio was 46/54. Diminished Zr incorporation with a decrease in the KOH:Pb, which was particularly notable at KOH:Pb ≤ 1.7, indicated that Zr ions required a higher base concentration for incorporation into the PZT perovskite structure than Ti ions did. The PZT particles exhibited a rhombohedral crystal structure at a Zr/Ti around 60/40; however, with a decrease to Zr/Ti < 50/50, a tetragonal phase also appeared. Unravelling of the above-described relationships will pave the way to further design of PZT ferroelectric (nano)particles in line with the needs of fundamental studies or practical application.

Supplementary Materials

The following supporting information can be downloaded at: https://www.mdpi.com/article/10.3390/cryst12111514/s1, Figure S1: SEM micrograph (SE image) of the PZT06 reaction product obtained through one-step precipitation process and hydrothermal reaction at 235 °C (12 h) at KOH:Pb = 20:1; Figure S2: SEM micrographs (a,b) of the PZT06 reaction product obtained through one-step precipitation process and hydrothermal reaction at 235 °C (12 h) at KOH:Pb = 3:1: (a) ⇒ SE image, b ⇒ BSE image; Figure S3: SEM micrographs of the PZT06 reaction product obtained through two-step precipitation process and hydrothermal reaction at 235 °C (12 h) (a,b) using the concentrations of Pb-, Zr- and Ti-precursors as shown in Table 1 (CTALH = 0.0112 mol/L, CZrOCl2 = 0.0168 mol/L, and cPb(CH3COO)2 = 0.035 mol/L) and (c,d) two-times larger concentrations of Pb-, Zr- and Ti-precursors (CTALH = 0.0224 mol/L, CZrOCl2 = 0.0336 mol/L, and cPb(CH3COO)2 = 0.07 mol/L). The concentrations of KOH were doubled in (c), resulting in KOH:Pb = 3:1, but in (d) remained the same as for the normal Pb- Zr-, and Ti-concentration experiments (0.1 mol/l), resulting in KOH:Pb = 1.5:1; Figure S4: Powder XRD pattern of the PZT07 reaction product obtained through two-step precipitation process and hydrothermal reaction at 235 °C (12 h) and at (a) KOH:Pb = 3:1, (b) KOH:Pb = 1.7:1, and (c) KOH:Pb = 1.5:1. The main diffraction lines of the rhombohedral (R) and tetragonal (T) phase were indexed according to ICDD PDF reference code 04-016-9524 (S.G.: R3c) and ICDD PDF reference code 01-070-4262 (S.G.: P4mm), respectively. The prevailing phase is denoted by a larger letter. The blue arrows indicate the occurrence of some characteristic diffractions of the tetragonal phase; Figure S5: Powder XRD pattern of the PZT08 reaction product obtained through two-step precipitation process and hydrothermal reaction at 235 °C (12 h) and at (a) OH:Pb = 3:1, (b) KOH:Pb = 1.7:1, and (c) KOH:Pb = 1.5:1. The main diffraction lines of the rhombohedral (R) and tetragonal (T) phase were indexed according to ICDD PDF reference code 01-078-4666 (S.G.: R3c) and ICDD PDF reference code 04-017-5715 (S.G.: P4mm), respectively. The prevailing phase is denoted by a larger letter. The blue arrows indicate the occurrence of some characteristic diffractions of the tetragonal phase.

Author Contributions

Conceptualization of the target composition and morphology, Z.K. and M.S.; conceptualization of the synthesis approach and methodology, M.M.K.; investigation, M.M.K.; writing—original draft preparation, M.M.K.; writing—review and editing, M.M.K. and M.S. All authors have read and agreed to the submitted version of the manuscript.

Funding

This research was funded by the Slovenian Research Agency (research program no. P2-0091) and the Ministry of Higher Education, Science and Technology, M-era.Net, under project SunToChem (no. 6081; contract no. C3330-19-252011).

Acknowledgments

The authors are grateful to Mihael Turkovic for his help in the extensive synthesis work.

Conflicts of Interest

The authors declare no conflict of interest.

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Figure 1. SEM micrographs of the PZT reaction product obtained through the one-step precipitation process and hydrothermal reaction at 235 °C (12 h) from the Zr- and Ti-precursors with initial Zr/Ti = 60/40 (PZT06) and at KOH:Pb = 30:1: (a,b,d) secondary electron (SE) images; (c,e) backscattered electron images (BSE) of the sample shown in SE images in (a) and (d), respectively.
Figure 1. SEM micrographs of the PZT reaction product obtained through the one-step precipitation process and hydrothermal reaction at 235 °C (12 h) from the Zr- and Ti-precursors with initial Zr/Ti = 60/40 (PZT06) and at KOH:Pb = 30:1: (a,b,d) secondary electron (SE) images; (c,e) backscattered electron images (BSE) of the sample shown in SE images in (a) and (d), respectively.
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Crystals 12 01514 g002 550
Figure 2. Powder XRD pattern of the PZT reaction product obtained through the one-step precipitation process and hydrothermal reaction at 235 °C (12 h) from the Zr- and Ti-precursors with the initial Zr/Ti = 60/40 (PZT06) and at (a) KOH:Pb = 30:1, (b) KOH:Pb = 20:1, (c) KOH:Pb = 6:1, (d) KOH:Pb = 5:1, (e) KOH:Pb = 4:1, and (f) KOH:Pb = 3:1. The main diffraction lines of rhombohedral (R) and tetragonal (T) phases were indexed according to ICDD PDF reference code 01-078-4666 and ICDD PDF reference code 04-014-6916, respectively. The prevailing phase is denoted by a larger font. The square designates the diffractions belonging to an unknown phase in the PZT06 sample, obtained at KOH:Pb = 3:1. The blue arrows indicate the occurrence of some characteristic diffractions of the tetragonal phase.
Figure 2. Powder XRD pattern of the PZT reaction product obtained through the one-step precipitation process and hydrothermal reaction at 235 °C (12 h) from the Zr- and Ti-precursors with the initial Zr/Ti = 60/40 (PZT06) and at (a) KOH:Pb = 30:1, (b) KOH:Pb = 20:1, (c) KOH:Pb = 6:1, (d) KOH:Pb = 5:1, (e) KOH:Pb = 4:1, and (f) KOH:Pb = 3:1. The main diffraction lines of rhombohedral (R) and tetragonal (T) phases were indexed according to ICDD PDF reference code 01-078-4666 and ICDD PDF reference code 04-014-6916, respectively. The prevailing phase is denoted by a larger font. The square designates the diffractions belonging to an unknown phase in the PZT06 sample, obtained at KOH:Pb = 3:1. The blue arrows indicate the occurrence of some characteristic diffractions of the tetragonal phase.
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Crystals 12 01514 g003 550
Figure 3. SEM micrographs (a–f) of the PZT06 reaction product obtained through one-step precipitation process and hydrothermal reaction at 235 °C (12 h) at (a) KOH:Pb = 20:1, (b) KOH:Pb = 6:1, (c,d) KOH:Pb = 4:1, and (e,f) KOH:Pb = 3:1: (a–c,e) ⇒ SE images; (d) and (f) ⇒ BSE images of the samples shown in the SE images in (c) and (e), respectively.
Figure 3. SEM micrographs (a–f) of the PZT06 reaction product obtained through one-step precipitation process and hydrothermal reaction at 235 °C (12 h) at (a) KOH:Pb = 20:1, (b) KOH:Pb = 6:1, (c,d) KOH:Pb = 4:1, and (e,f) KOH:Pb = 3:1: (a–c,e) ⇒ SE images; (d) and (f) ⇒ BSE images of the samples shown in the SE images in (c) and (e), respectively.
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Figure 4. (a) Size of the PbZrxTi1-xO3 (PZT) cubes (length of cube edge) versus KOH:Pb ratio for the PZT synthesized through one-step (PZT06, x = 0.6) and two-step precipitation approaches (PZT06 (x = 0.6), PZT07 (x = 0.7), PZT08 (x = 0.8)). (b) Histogram of the size distribution (length of cube edge) of the PZT06 cubes obtained through two-step precipitation approach and hydrothermal synthesis at 235 °C (12 h) at KOH:Pb = 1.7:1.
Figure 4. (a) Size of the PbZrxTi1-xO3 (PZT) cubes (length of cube edge) versus KOH:Pb ratio for the PZT synthesized through one-step (PZT06, x = 0.6) and two-step precipitation approaches (PZT06 (x = 0.6), PZT07 (x = 0.7), PZT08 (x = 0.8)). (b) Histogram of the size distribution (length of cube edge) of the PZT06 cubes obtained through two-step precipitation approach and hydrothermal synthesis at 235 °C (12 h) at KOH:Pb = 1.7:1.
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Figure 5. SEM micrographs (SE images) of the PZT06 reaction product obtained through two-step precipitation process and hydrothermal reaction at 235 °C (12 h) and at (a) KOH:Pb = 3:1, (b) KOH:Pb = 2:1, (c) KOH:Pb = 1.7:1, and (d) KOH:Pb = 1.5:1. The optimal morphology (well-separated small PZT particles (80–280 nm (Figure 4)) are shown in (c) (KOH:Pb = 1.7:1).
Figure 5. SEM micrographs (SE images) of the PZT06 reaction product obtained through two-step precipitation process and hydrothermal reaction at 235 °C (12 h) and at (a) KOH:Pb = 3:1, (b) KOH:Pb = 2:1, (c) KOH:Pb = 1.7:1, and (d) KOH:Pb = 1.5:1. The optimal morphology (well-separated small PZT particles (80–280 nm (Figure 4)) are shown in (c) (KOH:Pb = 1.7:1).
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Figure 6. Powder XRD pattern of the PZT06 reaction product obtained through two-step precipitation process and hydrothermal reaction at 235 °C (12 h) and at (a) KOH:Pb = 3:1, (b) KOH:Pb = 2:1, (c) KOH:Pb = 1.7:1, and (d) KOH:Pb = 1.5:1. The main diffraction lines of rhombohedral (R) and tetragonal (T) phase were indexed according to ICDD PDF reference code 01-070-4262 (S.G.: P4mm) and ICDD PDF reference code 04-012-9961 (S.G.: R3c), respectively. The prevailing phase is denoted by a larger letter. The blue arrows indicate the occurrence of some characteristic diffractions of the tetragonal phase.
Figure 6. Powder XRD pattern of the PZT06 reaction product obtained through two-step precipitation process and hydrothermal reaction at 235 °C (12 h) and at (a) KOH:Pb = 3:1, (b) KOH:Pb = 2:1, (c) KOH:Pb = 1.7:1, and (d) KOH:Pb = 1.5:1. The main diffraction lines of rhombohedral (R) and tetragonal (T) phase were indexed according to ICDD PDF reference code 01-070-4262 (S.G.: P4mm) and ICDD PDF reference code 04-012-9961 (S.G.: R3c), respectively. The prevailing phase is denoted by a larger letter. The blue arrows indicate the occurrence of some characteristic diffractions of the tetragonal phase.
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Crystals 12 01514 g007 550
Figure 7. SEM micrographs (SE images) of the PZT07 reaction product obtained through two-step precipitation process and hydrothermal reaction at 235 °C (12 h) and at (a) KOH:Pb = 3:1, (b) KOH:Pb = 2:1, (c) KOH:Pb = 1.7:1, and (d) KOH:Pb = 1.5:1.
Figure 7. SEM micrographs (SE images) of the PZT07 reaction product obtained through two-step precipitation process and hydrothermal reaction at 235 °C (12 h) and at (a) KOH:Pb = 3:1, (b) KOH:Pb = 2:1, (c) KOH:Pb = 1.7:1, and (d) KOH:Pb = 1.5:1.
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Figure 8. SEM micrographs (SE images) of the PZT08 reaction product obtained through two-step precipitation process and hydrothermal reaction at 235 °C (12 h) and at (a) KOH:Pb = 3:1, (b) KOH:Pb = 2:1, (c) KOH:Pb = 1.7:1, and (d) KOH:Pb = 1.5:1.
Figure 8. SEM micrographs (SE images) of the PZT08 reaction product obtained through two-step precipitation process and hydrothermal reaction at 235 °C (12 h) and at (a) KOH:Pb = 3:1, (b) KOH:Pb = 2:1, (c) KOH:Pb = 1.7:1, and (d) KOH:Pb = 1.5:1.
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Table
Table 1. Synthesis details in preparation of PbZrxTi1-xO3 (PZT) crystallites with the target x = 0.6 (PZT06), x = 0.7 (PZT07), and x = 0.8 (PZT08) compositions: concentrations of initial solutions before mixing together and concentrations in the autoclave before hydrothermal reactions.
Table 1. Synthesis details in preparation of PbZrxTi1-xO3 (PZT) crystallites with the target x = 0.6 (PZT06), x = 0.7 (PZT07), and x = 0.8 (PZT08) compositions: concentrations of initial solutions before mixing together and concentrations in the autoclave before hydrothermal reactions.
Target Composition (Synthesis Approach)Concentrations (mol/L)
Concentrations of Initial Solutions (mol/L)Concentrations in the PTFE Insert before Hydrothermal Reaction (mol/L)
PZT06 (one-step)TALH *0.1120.0112
ZrOCl2·8H2O0.1680.0168
Pb(OOCCH3)2·3H2O0.1750.035
KOH (OH:Pb)40:130:120:16:15:14:13:140:130:120:16:15:14:13:1
KOH (mol/L)3.52.61.750.530.440.350.261.4001.0500.7000.2100.1750.1400.110
PZT06 (two-step)TALH *0.112Precipitation Zr-Ti: (KOH:(Zr + Ti) = 7.8:1): pH = 70.0112
ZrOCl2·8H2O0.140.0168
Pb(OOCCH3)2·3H2O0.1750.035
KOH (OH:Pb)3:12:11.7:11.5:13:12:11.7:11.5:1
KOH (mol/L)0.7500.5000.4290.7350.10500.0700.06000.053
PZT07 (two-step)TALH *0.084Precipitation Zr-Ti: (KOH:(Zr + Ti) = 7.8:1): pH = 70.0084
ZrOCl2·8H2O0.1630.0196
Pb(OOCCH3)2·3H2O0.1750.035
KOH (OH:Pb)3:12:11.7:11.5:13:12:11.7:11.5:1
KOH (mol/L)0.7500.5000.4290.7350.1050.0700.0600.053
PZT08 (two-step)TALH *0.056Precipitation Zr-Ti: (KOH:(Zr + Ti) = 7.8:1): pH = 70.0056
ZrOCl2·8H2O0.1870.0224
Pb(OOCCH3)2·3H2O0.1750.035
KOH (OH:Pb)3:12:11.7:11.5:13:12:11.7:11.5:1
KOH (mol/L)0.7500.5000.4290.7350.1050.0700.0600.053
* TALH, titanium(IV) bis(ammonium lactato) dihydroxide.
Table
Table 2. Summary of the main characteristics of the PZT crystallites obtained by the one-step or two-step precipitation approach at different KOH:Pb ratios.
Table 2. Summary of the main characteristics of the PZT crystallites obtained by the one-step or two-step precipitation approach at different KOH:Pb ratios.
Proposed PZT Composition (Synthesis Approach)KOH:PbTypical Morphology (Average Composition as Obtained from EDS-Normalized to ABO3 Perovskite Structure)Average Length of Perovskite Cube Edge (Standard Deviation)
PZT06 (one-step)30:1Perovskite-cube-like (Pb0.83K0.06Zr0.39Ti0.68O3)Cube-like perovskite/1–2 μm
Zr-rich nanoparticles (Pb0.14K0.42Zr1.12Ti0.2O3)
20:1Perovskite cubes (PbZr0.56Ti0.45O3)Cubes/4 μm (1 μm)
6:1Perovskite cubes (PbZr0.55Ti0.44O3)Cubes/649 nm (80 nm)
5:1Perovskite cubes (PbZr0.5Ti0.5O3)Cubes/567 nm (72 nm)
4:1Perovskite cubes (PbZr0.56Ti0.42O3)Cubes/410 nm (48 nm)
3:1Perovskite dendrites (PbZr0.31Ti0.69O3)μm-size
Additional phase (Pb0.69Zr0.67Ti0.48O3)perovskite dendrite
PZT06 (two-step)3:1Perovskite cubes (PbZr0.55Ti0.43O3)Cubes/446 nm (54 nm)
2:1Perovskite cubes (PbZr0.52Ti0.48O3)Cubes/260 nm (31 nm)
1.7:1Perovskite cubes (PbZr0.46Ti0.54O3)Cubes/172 nm (36 nm)
1.5:1Perovskite aggregated and cube-like particles (Pb0.94Zr0.46Ti0.55O3)Cube-like/182 nm (48 nm)
PZT07 (two-step)3:01Perovskite cubes (PbZr0.58Ti0.41O3Cubes/613 nm (132 nm)
2:01Perovskite cubes (PbZr0.53Ti0.47O3)Cubes/301 nm (61 nm)
1.7:1Perovskite cubes (PbZr0.51Ti0.49O3)Cube-like/241 nm (46 nm)
1.5:1Perovskite (aggregated) cubes (PbZr0.47Ti0.53O3)Cube-like/185 nm (33 nm)
PZT08 (two-step)3:01Perovskite cubes (PbZr0.59Ti0.4O3Cubes/849 nm (117 nm)
2:01Perovskite cubes (PbZr0.5Ti0.5O3)Cube-like/355 nm (67 nm)
1.7:1Perovskite cubes (PbZr0.52Ti0.46O3)Cube-like/350 nm (75 nm)
1.5:1Perovskite dendrites (Pb0.94Zr0.31Ti0.72O3)Dendrites (several μm)
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Kržmanc, M.M.; Kutnjak, Z.; Spreitzer, M. Morphology Control of PbZrxTi1-xO3 Crystallites under Alkaline Hydrothermal Conditions. Crystals 2022, 12, 1514. https://doi.org/10.3390/cryst12111514

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Kržmanc MM, Kutnjak Z, Spreitzer M. Morphology Control of PbZrxTi1-xO3 Crystallites under Alkaline Hydrothermal Conditions. Crystals. 2022; 12(11):1514. https://doi.org/10.3390/cryst12111514

Chicago/Turabian Style

Kržmanc, Marjeta Maček, Zdravko Kutnjak, and Matjaž Spreitzer. 2022. "Morphology Control of PbZrxTi1-xO3 Crystallites under Alkaline Hydrothermal Conditions" Crystals 12, no. 11: 1514. https://doi.org/10.3390/cryst12111514

APA Style

Kržmanc, M. M., Kutnjak, Z., & Spreitzer, M. (2022). Morphology Control of PbZrxTi1-xO3 Crystallites under Alkaline Hydrothermal Conditions. Crystals, 12(11), 1514. https://doi.org/10.3390/cryst12111514

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