**Abstract**

This chapter reviews the laser floating zone (LFZ) technique, also known as the laser-heated pedestal growth (LHPG), focusing on the recently produced rareearth-doped oxyorthosilicate fibers. LFZ has been revealed as a suitable prototyping technique since high-quality crystals can be developed in short time with low consumption of precursor materials in a crucible-free processing that ensures to practically avoid by-products. Moreover, additional advantages are the possibility to treat and melt highly refractory materials together with the easy way for tailoring the final microstructural characteristics and this way the macroscopic physical properties. Thus, refractory rare-earth (RE) doped oxyorthosilicates following the formula RE2SiO5 have been recently produced by the LFZ technique for tuning laser emission parameters. The oxyorthosilicates have high chemical stability and allow incorporation of many rare-earth ions yielding different applications, such as laser host materials, gamma ray detectors or scintillators, environmental barrier coatings (EBCs) and waveguides, among others. Thus, different kinds of oxyorthosilicates were produced by the LFZ technique, and the detailed effects of the main processing parameters on crystal's characteristics are discussed in this chapter.

**Keywords:** laser floating zone, crystal growth, oxyorthosilicates, rare earths, single crystal, polycrystalline ceramics

## **1. Introduction**

The production of high-quality silicate-based single crystals is mainly accomplished by solid state and Czochralski methods ([1–9] and references therein). However, these methods require several amounts of material and the use of crucibles that can introduce external contamination. Moreover, expensive crucibles such as platinum or iridium and special atmospheres are usually necessary when the desired materials are refractory or their chemical reactivity can negatively affect the phase development. So, all these restrictions together with long processing time considerably increase the production costs, being not the most suitable approach for materials prototyping.

The micro-pulling down (μPD) and the floating zone (FZ) are alternative techniques to grow crystalline fibers from a melt [10–12]. The μPD technique is suitable for prototyping; however, the melt is continuously in contact with crucible, being

also applied low pulling rates. Concerning the FZ technique, the preform materials with cylindrical geometry (rods) are placed inside a mirror-like concave chamber provided with halogen lamps that allow the material melting in a small region. These techniques are complex and limited by the melting point of the materials.

The laser floating zone (LFZ) technique is similar to the FZ; however, a laser beam, guided into a closed chamber through a ZnSe window, is used to melt the top of a feed rod precursor material. Afterwards, a seed rod is immersed into the molten zone and pulled at a controlled pulling rate [13, 14]. This technique presents many advantages when compared with standard growth methods, namely the growth at high pulling rates, the synthesis of materials with very high melting temperature [15–17] and the most important one: it is a crucible-free process, thus avoiding any external related contamination [14, 18]. This way high purity crystals can be obtained in a short time from a small amount of raw material and minor energy consumption. Moreover, being a nonequilibrium process, metastable phases can be developed from the solid/liquid interface due to the very high thermal gradients [19]. **Figure 1** puts in evidence a scheme of the LFZ process.

The LFZ equipment comprises a laser system coupled to a reflective optical setup, composed by a *reflaxicon*, and a plane mirror and a parabolic mirror. The term *reflaxicon* was introduced in 1970 by Edmonds [20], and it describes a twostage pair of reflective linear axicon surfaces (**Figures 1** and **2**). As Edmonds [20] did not consider nonlinear axicons, all the applications that he proposed were afocal in nature. This reflective device essentially consists of a primary conical mirror and a larger secondary conical mirror coaxially located with respect to the primary. The function of this device is to convert a solid light beam into a hollow one in an essentially lossless manner (except for absorption at the mirror surface and other similar phenomena). This device is similar to the one patented by Martin in 1948 [21]. A circular crown-shaped laser beam is obtained by the mirror aiming to produce a uniform radial heating. In the LFZ process, after the *reflaxicon*, the plane mirror setted up 45° allows the laser beam reflection to the vertical position in the direction of the spherical or parabolic mirror. The rod precursor defines the crown size of the fiber produced, and a floating zone configuration is obtained [14, 18]. It must be noted that mirrors have a hole in their centers allowing feed and seed holders be placed in the optical axis [14]. Furthermore, the use of a closed chamber allows the growth under controlled atmosphere [22]. Additionally, the growth is controlled by a camera video system focused into the floating zone area allowing to observe the molten zone and particularly the melting and the crystallization interface [18].

**83**

properties [25, 26].

**Figure 2.**

**2. Oxyorthosilicates**

*Laser Floating Zone: General Overview Focusing on the Oxyorthosilicates Growth*

Andreeta et al. [14] have reported a good description of the LFZ systems, putting in evidence their modifications of the LFZ systems over the years. A highlight is made to all processes developed to control/modify the temperature gradient at the solid/liquid interface localized between the molten zone and feed/seed rods (**Figure 1**). Noteworthy is the method of electrically assisted laser floating zone (EALFZ) [23, 24] that explores a new mechanism for controlling the solidification process by applying an electric current through the solid/liquid interface. In the presence of an electric current, the solute transport depends not only on the local solute gradient but also on the electromigration of solute that will modify the composition and the characteristic length scale of the solute diffusion field ahead of crystals. The application of an electrical current strongly modified phase development, crystal shapes and effective distribution coefficients. The enhancement of nucleation rate and of the driving force for ion migration along the fiber axis promotes a strong increase in the grain alignment and consequently on the physical

Reflaxicon *performance noting light guiding with different colors to enhance comprehension.*

The LFZ method enables the development of high-quality light emitting materials and transparent conductive oxides with rare-earth doping [15, 27, 28] along with the growth of complex ceramic materials such as thermoelectric oxide materials [25, 29], high-temperature ceramic superconductors [19, 23, 26] and eutectic oxides [13, 30]. Alongside, by controlling the laser irradiance and the pulling rate, it is possible to determine the crystallization kinetics aiming to obtain highly oriented single or polycrystal-

Considering the LFZ characteristics, the focus of this work is on oxyorthosilicates, following the formula RE2SiO5 (RE = Gd, Lu and Nd). These silicates are highly refractory materials, and despite they present high chemical stability, it is possible to incorporate high concentrations of rare earth ions. Thus, they have attracted the attention of the researchers for long time, yielding different applications [2, 31]. Indeed, since their discovery by Toropov et al. [32], they have been applied as laser host materials [1–3, 9, 33–35], gamma ray detectors or scintillators [36], environmental barrier coatings (EBCs) [37] or, even, as waveguides [38]. The interest in this kind of compounds arose after the first study carried out by Hopkins et al. [39] based on the growth of the rare earth oxyapatites. However, it is important to highlight that these high refractory silicates were grown by the CZ method [1–5, 35–37, 39–41]. For example, Ryba-Romanovski et al. [1] developed solid state yellow lasers based on (LuxGd1-x)2SiO5:Sm crystals by CZ, while Wu et al. [41] have

line materials, with enhanced physical properties [16, 19, 24].

*DOI: http://dx.doi.org/10.5772/intechopen.90309*

**Figure 1.** *Laser floating zone setup, highlighting the molten zone.*

*Laser Floating Zone: General Overview Focusing on the Oxyorthosilicates Growth DOI: http://dx.doi.org/10.5772/intechopen.90309*

**Figure 2.** Reflaxicon *performance noting light guiding with different colors to enhance comprehension.*

Andreeta et al. [14] have reported a good description of the LFZ systems, putting in evidence their modifications of the LFZ systems over the years. A highlight is made to all processes developed to control/modify the temperature gradient at the solid/liquid interface localized between the molten zone and feed/seed rods (**Figure 1**). Noteworthy is the method of electrically assisted laser floating zone (EALFZ) [23, 24] that explores a new mechanism for controlling the solidification process by applying an electric current through the solid/liquid interface. In the presence of an electric current, the solute transport depends not only on the local solute gradient but also on the electromigration of solute that will modify the composition and the characteristic length scale of the solute diffusion field ahead of crystals. The application of an electrical current strongly modified phase development, crystal shapes and effective distribution coefficients. The enhancement of nucleation rate and of the driving force for ion migration along the fiber axis promotes a strong increase in the grain alignment and consequently on the physical properties [25, 26].

The LFZ method enables the development of high-quality light emitting materials and transparent conductive oxides with rare-earth doping [15, 27, 28] along with the growth of complex ceramic materials such as thermoelectric oxide materials [25, 29], high-temperature ceramic superconductors [19, 23, 26] and eutectic oxides [13, 30]. Alongside, by controlling the laser irradiance and the pulling rate, it is possible to determine the crystallization kinetics aiming to obtain highly oriented single or polycrystalline materials, with enhanced physical properties [16, 19, 24].

### **2. Oxyorthosilicates**

Considering the LFZ characteristics, the focus of this work is on oxyorthosilicates, following the formula RE2SiO5 (RE = Gd, Lu and Nd). These silicates are highly refractory materials, and despite they present high chemical stability, it is possible to incorporate high concentrations of rare earth ions. Thus, they have attracted the attention of the researchers for long time, yielding different applications [2, 31]. Indeed, since their discovery by Toropov et al. [32], they have been applied as laser host materials [1–3, 9, 33–35], gamma ray detectors or scintillators [36], environmental barrier coatings (EBCs) [37] or, even, as waveguides [38]. The interest in this kind of compounds arose after the first study carried out by Hopkins et al. [39] based on the growth of the rare earth oxyapatites. However, it is important to highlight that these high refractory silicates were grown by the CZ method [1–5, 35–37, 39–41]. For example, Ryba-Romanovski et al. [1] developed solid state yellow lasers based on (LuxGd1-x)2SiO5:Sm crystals by CZ, while Wu et al. [41] have

*Synthesis Methods and Crystallization*

also applied low pulling rates. Concerning the FZ technique, the preform materials with cylindrical geometry (rods) are placed inside a mirror-like concave chamber provided with halogen lamps that allow the material melting in a small region. These techniques are complex and limited by the melting point of the materials. The laser floating zone (LFZ) technique is similar to the FZ; however, a laser beam, guided into a closed chamber through a ZnSe window, is used to melt the top of a feed rod precursor material. Afterwards, a seed rod is immersed into the molten zone and pulled at a controlled pulling rate [13, 14]. This technique presents many advantages when compared with standard growth methods, namely the growth at high pulling rates, the synthesis of materials with very high melting temperature [15–17] and the most important one: it is a crucible-free process, thus avoiding any external related contamination [14, 18]. This way high purity crystals can be obtained in a short time from a small amount of raw material and minor energy consumption. Moreover, being a nonequilibrium process, metastable phases can be developed from the solid/liquid interface due to the very high thermal gradients

The LFZ equipment comprises a laser system coupled to a reflective optical setup, composed by a *reflaxicon*, and a plane mirror and a parabolic mirror. The term *reflaxicon* was introduced in 1970 by Edmonds [20], and it describes a twostage pair of reflective linear axicon surfaces (**Figures 1** and **2**). As Edmonds [20] did not consider nonlinear axicons, all the applications that he proposed were afocal in nature. This reflective device essentially consists of a primary conical mirror and a larger secondary conical mirror coaxially located with respect to the primary. The function of this device is to convert a solid light beam into a hollow one in an essentially lossless manner (except for absorption at the mirror surface and other similar phenomena). This device is similar to the one patented by Martin in 1948 [21]. A circular crown-shaped laser beam is obtained by the mirror aiming to produce a uniform radial heating. In the LFZ process, after the *reflaxicon*, the plane mirror setted up 45° allows the laser beam reflection to the vertical position in the direction of the spherical or parabolic mirror. The rod precursor defines the crown size of the fiber produced, and a floating zone configuration is obtained [14, 18]. It must be noted that mirrors have a hole in their centers allowing feed and seed holders be placed in the optical axis [14]. Furthermore, the use of a closed chamber allows the growth under controlled atmosphere [22]. Additionally, the growth is controlled by a camera video system focused into the floating zone area allowing to observe the molten zone and particularly the melting and the crystallization interface [18].

[19]. **Figure 1** puts in evidence a scheme of the LFZ process.

**82**

**Figure 1.**

*Laser floating zone setup, highlighting the molten zone.*

recently grown Cu co-doped Ce:Lu2SiO5 crystals at 1.5 mm h<sup>−</sup><sup>1</sup> using a iridium crucible under nitrogen atmosphere for application as scintillators. Furthermore, other approaches for oxyorthosilicates production have been employed during the last years using different methods, like pulsed laser deposition [42], sol–gel [43] or solid-state diffusional process [44]. On the other hand, their production by the LFZ technique is more recent [18, 45–47]; besides, there are two experiments performed in the 1980s decade by de la Fuente et al. [33] and Black et al. [34], who produced GdNdSiO5 and 7Gd2O3•9SiO2:Nd materials applying a high laser power (~185 W).

Aiming to develop new laser materials, Rey-García et al. [18, 46, 47] have recently produced a sort of gadolinium-lutetium oxyorthosilicate materials at low laser powers (<100 W) and pulling rates two to three times faster than those used by Czochralski or other standard methods (1-3 mm h<sup>−</sup><sup>1</sup> ). Thus, transparent fibers of Gd2SiO5 [18], (Gd0.3Lu0.7)2SiO5 [46] and 5 mol% Y3+:(Gd0.3Lu0.7)2SiO5 [47] have been obtained at 10 mm h<sup>−</sup><sup>1</sup> in air under atmospheric pressure presenting high crystallinity degree. These single crystals present excellent photonic properties that make them useful to be employed as laser host materials due to the Gd3+ charger transfer band (CTB) that favors the transfer processes with 4f <sup>7</sup> transitions from the 8 S7/2 ground state to energy levels of the dopant element [48–50]. Regarding compositional aspects, despite the similarity observed in these single crystals produced by LFZ, the growing processes based on stoichiometric mixtures of Lu2O3 or Nd2O3 with SiO2 bring considerable deviations on the phases diagram associated to crystallization paths that can induce materials evaporation or phases rearrangement [45]. Likewise, the LFZ suitability could be sometimes compromised by precursor's properties, nominal compositions or growing conditions. Consequently, remarkable crack formation can be developed due to internal stress mainly induced by the biaxial character of these silicates and the experimental growing parameters [18].

Summarizing, this chapter will highlight the suitability of the LFZ technique on developing compact and miniaturized crystals envisaging new photonic devices, through the production of low volume bulks with an appropriate geometry based on oxyorthosilicates. The optical fundaments of the LFZ technique together with practical aspects relating to oxyorthosilicates production will be described before showing the microstructural and photonic properties of the materials produced. The idea is to demonstrate the LFZ technique as a suitable, time-saving and economic process for laser materials prototyping compared with traditional techniques [14, 40].

#### **3. Experimental**

The extrusion process is the most common way to prepare the precursor rod cylinders for the LFZ process, since it is a simple method, not requiring special equipment or additional hands. Thus, the commercial raw oxide powders are mixed, according to the desired stoichiometry, and reduced into grain size with an agate ball mill for 2 hours at 200 rpm. The purity of the precursors depends on the desired application, being used, in this study, powders of 5–6 N of purity since photonics applications are envisaging. Aiming to bind the powder mixture for extrusion process, polyvinyl alcohol (PVA, 0.1 g ml<sup>−</sup><sup>1</sup> ) is added in mashing the powders until a compact and plastic paste is achieved. Then, the obtained clay is extruded into cylindrical rods, with diameters depending on the material applications. In the case of the oxyorthosilicates, diameters ranging 1.5–2.0 mm were selected.

After extrusion, the cylindrical rods are dried in air, being ready to be used as feed and seed materials. However, in the LFZ process, single crystals can also be used as the seed rods [14], favoring the formation of a single crystalline fiber. This approach helps laser processing and allows enhancing the structural

**85**

*Laser Floating Zone: General Overview Focusing on the Oxyorthosilicates Growth*

**Power (W)**

Gd2SiO5 GSO 72 Gd2SiO5 Crystal (Lu0.1Gd0.9)2SiO5 LGSO-1 67 (Lu0.12Gd0.88)2SiO5 Crystal (Lu0.3Gd0.7)2SiO5 LGSO-3 58 (Lu0.31Gd0.69)2SiO5 Crystal (Lu0.5Gd0.5)2SiO5 LGSO-5 64 (Lu0.53Gd0.47)2SiO5 Crystal Lu2SiO5 LSO-10 92 Lu2SiO5/Lu2O3 Eutectics Nd2SiO5 NSO-10 69 Nd2SiO5/Nd9.33(SiO4)6O2 Biphasic

characteristics of the single crystal fiber produced. However, this approach was

 *in air by LFZ.*

The LFZ equipment employed for the oxyorthosilicates growth comprise a 200 W CO2 laser (Spectron, GSI group) coupled to a reflective optical set-up described in the previous section, Optical Fundaments. Once seed and feed fibers are placed on the respective holders, a fast growth process was performed aiming to obtain dense precursor materials. This densification step occurred at 100 mm h<sup>−</sup><sup>1</sup> pulling rate and promotes the PVA decomposition, the formation of the desired phases and enhances the rods mechanical properties. A molten zone is formed by irradiating the densified rods with the CO2 laser. The fibers were grown in descen-

(crystallization step). Simultaneously during growth, the feed and seed rods rotated at 5 rpm in opposite direction. This procedure favors the mixing of precursors in the melt, homogenizes the temperature of the molten material and contributes to reduce the thermal stresses. In the case of oxyorthosilicate single crystals based on (LuxGd1-x)2SiO5 (x = 0–1), the growing process should end by reducing the laser power gradually. This procedure is very important to reduce the thermal stresses

**Table 1** summarizes the experimental conditions to grow oxyorthosilicate

ing points, (2420, 2490 and 2233°C, respectively), the slight variation of the laser power irradiance well matches with this small melting point variation. Despite the experimental conditions are similar, the fibers developed varied from single crystal (GSO and derived silicates) to eutectic (LSO derived) and biphasic (NSO derived) ceramics due to specific characteristic of each phase diagram. Concomitantly, the most remarkable characteristics of the oxyorthosilicates produced in air by LFZ will

Regarding structural properties, the silicates having the formula RE2SiO5 are all monoclinic, presenting P21/c (Gd2SiO5, [18]) or C2/c (Lu2SiO5, [45]) space groups depending on the rare earth ions present (**Figure 3**) [46, 51]. This structure provokes their biaxial character that compromises their crystallization, resulting in internal crack formation when LFZ processing is carried out in air and the cooling is not gradually performed [18, 47]. **Figure 4** shows the XRD powder diffractogram of the Gd, Lu and Nd oxyorthosilicates presented in this chapter. It should be noted

in air by LFZ. Considering the Gd2O3, Lu2O3 and Nd2O3 melt-

in air at atmospheric pressure,

**Obtained composition Fiber type**

declined for oxyorthosilicates due to their high melting points.

*All fibers have diameters of 1.5 mm for all samples except Lu2SiO5 that have 2 mm.*

dent direction from this molten region at 10 mm h<sup>−</sup><sup>1</sup>

and, therefore, avoiding the crack formation.

fibers at 10 mm h<sup>−</sup><sup>1</sup>

**Table 1.**

be described below.

**4. Results**

*DOI: http://dx.doi.org/10.5772/intechopen.90309*

**acronym**

**Nominal formula Sample** 

*Oxyorthosilicates fibers grown at 10 mm h<sup>−</sup><sup>1</sup>*


*Laser Floating Zone: General Overview Focusing on the Oxyorthosilicates Growth DOI: http://dx.doi.org/10.5772/intechopen.90309*

#### **Table 1.**

*Synthesis Methods and Crystallization*

been obtained at 10 mm h<sup>−</sup><sup>1</sup>

**3. Experimental**

process, polyvinyl alcohol (PVA, 0.1 g ml<sup>−</sup><sup>1</sup>

8

recently grown Cu co-doped Ce:Lu2SiO5 crystals at 1.5 mm h<sup>−</sup><sup>1</sup>

by Czochralski or other standard methods (1-3 mm h<sup>−</sup><sup>1</sup>

transfer band (CTB) that favors the transfer processes with 4f <sup>7</sup>

crucible under nitrogen atmosphere for application as scintillators. Furthermore, other approaches for oxyorthosilicates production have been employed during the last years using different methods, like pulsed laser deposition [42], sol–gel [43] or solid-state diffusional process [44]. On the other hand, their production by the LFZ technique is more recent [18, 45–47]; besides, there are two experiments performed in the 1980s decade by de la Fuente et al. [33] and Black et al. [34], who produced GdNdSiO5 and 7Gd2O3•9SiO2:Nd materials applying a high laser power (~185 W). Aiming to develop new laser materials, Rey-García et al. [18, 46, 47] have recently produced a sort of gadolinium-lutetium oxyorthosilicate materials at low laser powers (<100 W) and pulling rates two to three times faster than those used

of Gd2SiO5 [18], (Gd0.3Lu0.7)2SiO5 [46] and 5 mol% Y3+:(Gd0.3Lu0.7)2SiO5 [47] have

crystallinity degree. These single crystals present excellent photonic properties that make them useful to be employed as laser host materials due to the Gd3+ charger

S7/2 ground state to energy levels of the dopant element [48–50]. Regarding compositional aspects, despite the similarity observed in these single crystals produced by LFZ, the growing processes based on stoichiometric mixtures of Lu2O3 or Nd2O3 with SiO2 bring considerable deviations on the phases diagram associated to crystallization paths that can induce materials evaporation or phases rearrangement [45]. Likewise, the LFZ suitability could be sometimes compromised by precursor's properties, nominal compositions or growing conditions. Consequently, remarkable crack formation can be developed due to internal stress mainly induced by the biaxial character of these silicates and the experimental growing parameters [18]. Summarizing, this chapter will highlight the suitability of the LFZ technique on developing compact and miniaturized crystals envisaging new photonic devices, through the production of low volume bulks with an appropriate geometry based on oxyorthosilicates. The optical fundaments of the LFZ technique together with practical aspects relating to oxyorthosilicates production will be described before showing the microstructural and photonic properties of the materials produced. The idea is to demonstrate the LFZ technique as a suitable, time-saving and economic process for

laser materials prototyping compared with traditional techniques [14, 40].

The extrusion process is the most common way to prepare the precursor rod cylinders for the LFZ process, since it is a simple method, not requiring special equipment or additional hands. Thus, the commercial raw oxide powders are mixed, according to the desired stoichiometry, and reduced into grain size with an agate ball mill for 2 hours at 200 rpm. The purity of the precursors depends on the desired application, being used, in this study, powders of 5–6 N of purity since photonics applications are envisaging. Aiming to bind the powder mixture for extrusion

a compact and plastic paste is achieved. Then, the obtained clay is extruded into cylindrical rods, with diameters depending on the material applications. In the case

After extrusion, the cylindrical rods are dried in air, being ready to be used as feed and seed materials. However, in the LFZ process, single crystals can also be used as the seed rods [14], favoring the formation of a single crystalline fiber. This approach helps laser processing and allows enhancing the structural

of the oxyorthosilicates, diameters ranging 1.5–2.0 mm were selected.

in air under atmospheric pressure presenting high

using a iridium

). Thus, transparent fibers

) is added in mashing the powders until

transitions from the

**84**

*Oxyorthosilicates fibers grown at 10 mm h<sup>−</sup><sup>1</sup> in air by LFZ.*

characteristics of the single crystal fiber produced. However, this approach was declined for oxyorthosilicates due to their high melting points.

The LFZ equipment employed for the oxyorthosilicates growth comprise a 200 W CO2 laser (Spectron, GSI group) coupled to a reflective optical set-up described in the previous section, Optical Fundaments. Once seed and feed fibers are placed on the respective holders, a fast growth process was performed aiming to obtain dense precursor materials. This densification step occurred at 100 mm h<sup>−</sup><sup>1</sup> pulling rate and promotes the PVA decomposition, the formation of the desired phases and enhances the rods mechanical properties. A molten zone is formed by irradiating the densified rods with the CO2 laser. The fibers were grown in descendent direction from this molten region at 10 mm h<sup>−</sup><sup>1</sup> in air at atmospheric pressure, (crystallization step). Simultaneously during growth, the feed and seed rods rotated at 5 rpm in opposite direction. This procedure favors the mixing of precursors in the melt, homogenizes the temperature of the molten material and contributes to reduce the thermal stresses. In the case of oxyorthosilicate single crystals based on (LuxGd1-x)2SiO5 (x = 0–1), the growing process should end by reducing the laser power gradually. This procedure is very important to reduce the thermal stresses and, therefore, avoiding the crack formation.

**Table 1** summarizes the experimental conditions to grow oxyorthosilicate fibers at 10 mm h<sup>−</sup><sup>1</sup> in air by LFZ. Considering the Gd2O3, Lu2O3 and Nd2O3 melting points, (2420, 2490 and 2233°C, respectively), the slight variation of the laser power irradiance well matches with this small melting point variation. Despite the experimental conditions are similar, the fibers developed varied from single crystal (GSO and derived silicates) to eutectic (LSO derived) and biphasic (NSO derived) ceramics due to specific characteristic of each phase diagram. Concomitantly, the most remarkable characteristics of the oxyorthosilicates produced in air by LFZ will be described below.

#### **4. Results**

Regarding structural properties, the silicates having the formula RE2SiO5 are all monoclinic, presenting P21/c (Gd2SiO5, [18]) or C2/c (Lu2SiO5, [45]) space groups depending on the rare earth ions present (**Figure 3**) [46, 51]. This structure provokes their biaxial character that compromises their crystallization, resulting in internal crack formation when LFZ processing is carried out in air and the cooling is not gradually performed [18, 47]. **Figure 4** shows the XRD powder diffractogram of the Gd, Lu and Nd oxyorthosilicates presented in this chapter. It should be noted

**Figure 3.** *Structural scheme of P21/c and C2/c spatial groups [46].*

**Figure 4.**

*XRD diffractograms of the oxyorthosilicates produced by LFZ in air at 10 mm h<sup>−</sup><sup>1</sup> [18, 45–47].*

that the change from P21/c (Gd2SiO5 and (Lu0.12Gd0.88)2SiO5) to C2/c space group is most visible in the diffractograms at 2θ ranging from 20 to 30°.

Following the structural overview about oxyorthosilicates, the Raman spectroscopy analysis can be divided in two groups or families considering the total number of vibrational modes together with the shape of the high frequency region. Thus, assuming the Voron'ko et al. [8] notation, oxyorthosilicates can be distinguished among **A-type** and **B-type** silicates depending on whether a triplet or a doublet, respectively, appears inside the (ν1 + ν3) region [8, 9, 18, 45–47]. This way, the Raman spectra can be divided in four vibrational regions denoted as ν3, (ν1 + ν3), ν4 and νext + ν<sup>2</sup> (**Figure 5**) [8]. The modes (ν1)–(ν4) correspond to free internal vibrations of the

**87**

**Figure 5.**

*oxyorthosilicates grown in air by LFZ [18, 45–47].*

*Laser Floating Zone: General Overview Focusing on the Oxyorthosilicates Growth*

while the external oscillations produced by the translation of the [MO4]-complexes are ascribed to the νext mode [8, 46, 52]. In addition, the modes related to rare earth ions and RE-O stretching vibrations are also placed inside the (νext + ν2) region.

One of the most important oxyorthosilicates is gadolinium silicate (Gd2SiO5, GSO) due to the Gd3+ charger transfer band (CTB) that favors the transfer pro-

Transparent crystalline fibers with a yellowish aspect at naked eye (**Figure 6a**) were grown in 2017 by Rey-García et al. [18] using the LFZ technique. These fibers present a similar aspect to the ones obtained by Takagi et al. using Czochralski method [53]. Moreover, the LFZ fibers were developed in air at higher pulling rates. SEM analysis reveals a homogeneous fiber without visible grain boundaries (**Figure 6b**), thus suggesting a single crystal character. Furthermore, the EDS analysis performed confirms this homogeneity and putting in evidence the uniform elemental composi-

Following the structural analysis, the XRD powders diffractogram shown in **Figure 3** well matches with the 04–009-2670 XRD card (International Centre for Diffraction Data, 2019 [54]) putting in evidence the crystallinity and the monophasic nature of the monoclinic P21/c Gd2(SiO4)O oxyorthosilicate. Moreover, XRD scan along the longitudinal section of a polished fiber matching the diffraction maxima corresponding to {h 0 0} planes, suggesting a monocrystalline character. Aiming to confirm this evidence, 3D pole figures on longitudinal and transversal cross sections of the fibers were acquired (**Figure 7**). The crystallographic texture measurements confirmed the production of Gd2SiO5 single crystal fibers by LFZ, since only one high intense peak was observed in both sections. This type of morphology is potentiated by the strong thermal gradient that exists at the crystallization interface in the LFZ process [55]. So, in conclusion, these observations, namely the preferential orientation and the absence of grain boundaries in SEM analysis, permit to confirm the single crystal character of the GSO fibers grown by LFZ. In addition, the Raman spectroscopy analysis (**Figure 5**) of the GSO samples put in evidence several narrow

<sup>4</sup><sup>−</sup> complex in the reduced C1 symmetry of the monoclinic lattice,

S7/2 to energy levels of the dopant element [48–50].

*DOI: http://dx.doi.org/10.5772/intechopen.90309*

**4.1 Gadolinium oxyorthosilicate (GSO)**

tion corresponding to Gd2SiO5 stoichiometry.

lines, as expected for a low-symmetry crystalline structure [18].

*Raman spectra performed under excitation of 441.6 nm line of a He-Cd laser (Kimmon IK series) of the* 

cesses from the ground state 8

tetrahedral [SiO4]

tetrahedral [SiO4] <sup>4</sup><sup>−</sup> complex in the reduced C1 symmetry of the monoclinic lattice, while the external oscillations produced by the translation of the [MO4]-complexes are ascribed to the νext mode [8, 46, 52]. In addition, the modes related to rare earth ions and RE-O stretching vibrations are also placed inside the (νext + ν2) region.

## **4.1 Gadolinium oxyorthosilicate (GSO)**

*Synthesis Methods and Crystallization*

**86**

**Figure 3.**

**Figure 4.**

*Structural scheme of P21/c and C2/c spatial groups [46].*

that the change from P21/c (Gd2SiO5 and (Lu0.12Gd0.88)2SiO5) to C2/c space group is

 *[18, 45–47].*

Following the structural overview about oxyorthosilicates, the Raman spectroscopy analysis can be divided in two groups or families considering the total number of vibrational modes together with the shape of the high frequency region. Thus, assuming the Voron'ko et al. [8] notation, oxyorthosilicates can be distinguished among **A-type** and **B-type** silicates depending on whether a triplet or a doublet, respectively, appears inside the (ν1 + ν3) region [8, 9, 18, 45–47]. This way, the Raman spectra can be divided in four vibrational regions denoted as ν3, (ν1 + ν3), ν4 and νext + ν<sup>2</sup> (**Figure 5**) [8]. The modes (ν1)–(ν4) correspond to free internal vibrations of the

most visible in the diffractograms at 2θ ranging from 20 to 30°.

*XRD diffractograms of the oxyorthosilicates produced by LFZ in air at 10 mm h<sup>−</sup><sup>1</sup>*

One of the most important oxyorthosilicates is gadolinium silicate (Gd2SiO5, GSO) due to the Gd3+ charger transfer band (CTB) that favors the transfer processes from the ground state 8 S7/2 to energy levels of the dopant element [48–50]. Transparent crystalline fibers with a yellowish aspect at naked eye (**Figure 6a**) were grown in 2017 by Rey-García et al. [18] using the LFZ technique. These fibers present a similar aspect to the ones obtained by Takagi et al. using Czochralski method [53]. Moreover, the LFZ fibers were developed in air at higher pulling rates. SEM analysis reveals a homogeneous fiber without visible grain boundaries (**Figure 6b**), thus suggesting a single crystal character. Furthermore, the EDS analysis performed confirms this homogeneity and putting in evidence the uniform elemental composition corresponding to Gd2SiO5 stoichiometry.

Following the structural analysis, the XRD powders diffractogram shown in **Figure 3** well matches with the 04–009-2670 XRD card (International Centre for Diffraction Data, 2019 [54]) putting in evidence the crystallinity and the monophasic nature of the monoclinic P21/c Gd2(SiO4)O oxyorthosilicate. Moreover, XRD scan along the longitudinal section of a polished fiber matching the diffraction maxima corresponding to {h 0 0} planes, suggesting a monocrystalline character. Aiming to confirm this evidence, 3D pole figures on longitudinal and transversal cross sections of the fibers were acquired (**Figure 7**). The crystallographic texture measurements confirmed the production of Gd2SiO5 single crystal fibers by LFZ, since only one high intense peak was observed in both sections. This type of morphology is potentiated by the strong thermal gradient that exists at the crystallization interface in the LFZ process [55]. So, in conclusion, these observations, namely the preferential orientation and the absence of grain boundaries in SEM analysis, permit to confirm the single crystal character of the GSO fibers grown by LFZ. In addition, the Raman spectroscopy analysis (**Figure 5**) of the GSO samples put in evidence several narrow lines, as expected for a low-symmetry crystalline structure [18].

#### **Figure 5.**

*Raman spectra performed under excitation of 441.6 nm line of a He-Cd laser (Kimmon IK series) of the oxyorthosilicates grown in air by LFZ [18, 45–47].*

#### **Figure 6.**

*(a) Photograph of GSO sample [18] and (b) corresponding SEM micrograph.*

**Figure 7.**

*XRD 3D pole figures of (a) longitudinal section, obtained for 2θ = 30.7°, corresponding to the (3 0 0) plane and (b) transversal cross section for (1 2 1) crystallographic plane of GSO fiber [18].*

The optical spectroscopy characterization, performed from the ultraviolet to the near infrared spectral region, by photoluminescence and photoluminescence excitation suggests that GSO fibers are in fact suitable materials to be doped with rare earth active ions envisaging developing optical efficient laser materials [18]. The spectrum is mainly characterized by a series of sharp lines in the ultraviolet region corresponding to the intra 4f <sup>7</sup> transitions of the Gd3+ ions. In fact, their excitation with ultraviolet photons promotes intra 4f <sup>7</sup> transitions of the Gd3+ ions, and therefore, the energy transfer observed provokes internal f→f transitions of trivalent dopant ions [56–58].

## **4.2 Lutetium and gadolinium oxyorthosilicate (LGSO)**

The interest of researchers has progressively gone *in crescendo* to mixed oxyorthosilicates of lutetium and gadolinium (LGSO) [1, 9, 59, 60] due to the following reasons:


**89**

**Figure 8.**

*Transmission spectra and photographs of LGSO fibers in the UV range [46].*

*Laser Floating Zone: General Overview Focusing on the Oxyorthosilicates Growth*

crystalline fibers were successfully produced by LFZ in air at 10 mm h<sup>−</sup><sup>1</sup>

iii.Finally, comparing the melting points of Lu2O3 (2490°C) and Gd2O3

(2420°C), the introduction of the second one on pure LSO materials should

[46]. Thus,

Analogous to what has been previously mentioned, Czochralski (CZ) method has been extensively used to develop LGSO [1, 9, 52] since Loutts et al. [61] produced LGSO for the first time in 1997. Thus, lutetium-gadolinium oxyorthosilicate

three compositions based on (LuxGd1-x)2SiO5 formula were developed, establishing the doping level as x = 0.1 (LGSO-1), 0.3 (LGSO-3) and 0.5 (LGSO-5). Plane parallel-polished fragments of each one is shown in **Figure 8**. The transparency degree is clearly observed at naked eye, being not gradual with lutetium amount. In fact, LGSO-1 and LGSO-5 are translucent fibers, owning the first a yellowish tone like to that observed for pure GSO fibers. On the other hand, LGSO-3 sample is transparent, being distinguishable the colors and letters of the background image. Transmission spectra (**Figure 8**) corroborate this appearance. Transmittance values from 50% up to 77% along the visible range are observed. In addition, it must be noted that the transfer bands of the Gd3+ have resulted for the LGSO-3 fibers higher in intensity than pure GSO, highlighting this crystal as optimal host laser material. On the other hand, the EDS analysis shown that LGSO crystalline fibers produced

by LFZ present compositions close to the initial mixtures, in opposite to compositional dissimilarity observed on LGSO materials developed by conventional CZ method [1, 9, 52]. The expected structural change at x = 0.17 coming from the Lu amount matches with that reported by literature [1, 9, 52, 62]. Thus, LGSO-1 presents the monoclinic P21/c structure, while the other two have a monoclinic C2/c structure, as can be deduced from the diffractograms shown in **Figure 4**. This way, LGSO-1 matched with the 01-080-9851 XRD card ICDD, while LGSO-3 and LGSO-5 are isostructural with the 00-061-0488 and the 00-061-0369 XRD cards, respectively [54]. The phase transition observed with lutetium addition is explained from atomic size and the differences of nearest surrounding rare earth ions, as reported Ryba-Romanowski et al. [63]. In fact, GSO lattice present Gd1 and Gd2 sites with different coordination number and local symmetries (CN = 9, C3v and CN = 7, Cs, respectively), promoting the polyhedrons GdO9 and GdO7. On the other side, LSO

*DOI: http://dx.doi.org/10.5772/intechopen.90309*

slightly reduce the LGSO melting point.

*Laser Floating Zone: General Overview Focusing on the Oxyorthosilicates Growth DOI: http://dx.doi.org/10.5772/intechopen.90309*

iii.Finally, comparing the melting points of Lu2O3 (2490°C) and Gd2O3 (2420°C), the introduction of the second one on pure LSO materials should slightly reduce the LGSO melting point.

Analogous to what has been previously mentioned, Czochralski (CZ) method has been extensively used to develop LGSO [1, 9, 52] since Loutts et al. [61] produced LGSO for the first time in 1997. Thus, lutetium-gadolinium oxyorthosilicate crystalline fibers were successfully produced by LFZ in air at 10 mm h<sup>−</sup><sup>1</sup> [46]. Thus, three compositions based on (LuxGd1-x)2SiO5 formula were developed, establishing the doping level as x = 0.1 (LGSO-1), 0.3 (LGSO-3) and 0.5 (LGSO-5). Plane parallel-polished fragments of each one is shown in **Figure 8**. The transparency degree is clearly observed at naked eye, being not gradual with lutetium amount. In fact, LGSO-1 and LGSO-5 are translucent fibers, owning the first a yellowish tone like to that observed for pure GSO fibers. On the other hand, LGSO-3 sample is transparent, being distinguishable the colors and letters of the background image. Transmission spectra (**Figure 8**) corroborate this appearance. Transmittance values from 50% up to 77% along the visible range are observed. In addition, it must be noted that the transfer bands of the Gd3+ have resulted for the LGSO-3 fibers higher in intensity than pure GSO, highlighting this crystal as optimal host laser material.

On the other hand, the EDS analysis shown that LGSO crystalline fibers produced by LFZ present compositions close to the initial mixtures, in opposite to compositional dissimilarity observed on LGSO materials developed by conventional CZ method [1, 9, 52]. The expected structural change at x = 0.17 coming from the Lu amount matches with that reported by literature [1, 9, 52, 62]. Thus, LGSO-1 presents the monoclinic P21/c structure, while the other two have a monoclinic C2/c structure, as can be deduced from the diffractograms shown in **Figure 4**. This way, LGSO-1 matched with the 01-080-9851 XRD card ICDD, while LGSO-3 and LGSO-5 are isostructural with the 00-061-0488 and the 00-061-0369 XRD cards, respectively [54].

The phase transition observed with lutetium addition is explained from atomic size and the differences of nearest surrounding rare earth ions, as reported Ryba-Romanowski et al. [63]. In fact, GSO lattice present Gd1 and Gd2 sites with different coordination number and local symmetries (CN = 9, C3v and CN = 7, Cs, respectively), promoting the polyhedrons GdO9 and GdO7. On the other side, LSO

**Figure 8.** *Transmission spectra and photographs of LGSO fibers in the UV range [46].*

*Synthesis Methods and Crystallization*

**Figure 6.**

**Figure 7.**

region corresponding to the intra 4f <sup>7</sup>

trivalent dopant ions [56–58].

optical properties.

lowing reasons:

excitation with ultraviolet photons promotes intra 4f <sup>7</sup>

*(b) transversal cross section for (1 2 1) crystallographic plane of GSO fiber [18].*

*(a) Photograph of GSO sample [18] and (b) corresponding SEM micrograph.*

**4.2 Lutetium and gadolinium oxyorthosilicate (LGSO)**

The optical spectroscopy characterization, performed from the ultraviolet to the near infrared spectral region, by photoluminescence and photoluminescence excitation suggests that GSO fibers are in fact suitable materials to be doped with rare earth active ions envisaging developing optical efficient laser materials [18]. The spectrum is mainly characterized by a series of sharp lines in the ultraviolet

*XRD 3D pole figures of (a) longitudinal section, obtained for 2θ = 30.7°, corresponding to the (3 0 0) plane and* 

and therefore, the energy transfer observed provokes internal f→f transitions of

The interest of researchers has progressively gone *in crescendo* to mixed oxyorthosilicates of lutetium and gadolinium (LGSO) [1, 9, 59, 60] due to the fol-

i.Lu2O3 precursor is expensive, increasing the production cost of photonic materials. This way, the co-doping with gadolinium ions, using as raw material Gd2O3, allows reducing the cost without affecting the structural and

ii.Gadolinium oxyorthosilicate single crystals tend to develop cracks during growth. Considering this handicap, lutetium doping has been employed aiming to reduce thermal stress and, therefore, avoiding crack formation.

transitions of the Gd3+ ions. In fact, their

transitions of the Gd3+ ions,

**88**

lattice present both lutetium ions, and therefore, the LuO6 (Lu1) and LuO7 (Lu2) polyhedrons present the Cs local symmetry. The former has only one plane of symmetry, while the C3v point group presents higher steric effect. Additionally, despite the smaller ionic radius of the Lu3+, its inclusion into the monoclinic P21/c unit cell strongly affects the crystalline structure. Concomitantly, the GSO structure type allows low Lu doping. In opposite, the C2/c type structure presents minor steric effect and higher symmetry degrees of freedom, allowing the introduction of large size ions such as Gd3+ or Ce3+ on the Lu sites. Consequently, LGSO-3 and LGSO-5 samples have the C2/c crystalline structure, which is larger in size than P21/c (**Table 2**). On the other hand, **Table 2** shows how introduction of Lu decreases the volume of the cell together with an increase of the density. Concerning Raman spectroscopy characterization, LGSO-3 sample presents an intermediate spectrum between the GSO and LSO (**Figure 5**). In fact, when (ν1 + ν3) region is revised, LGSO-1 relates to A-type, like GSO structure, while LGSO-3 and LGSO-5 spectrum shape shows the typical doublet of B-type silicates, such as undoped LSO. Finally, the transmission studies of LGSO samples allow concluding that the Gd3+ ions are optically active. In fact, an intra-ionic absorption due to the energy transfer band ascribed to 8 S7/2 → 6 IJ transition is observed, and this band is the highest for LGSO-3 sample, the one that is the most transparent and presents lower cracks. All these considerations allow to consider the LGSO-3 fibers as the most suitable host material for photonic applications [46].

### **4.3 Rare-earth-doped lutetium and gadolinium oxyorthosilicates (LGSO:RE)**

Once the best laser host properties were determined by developing the initial Gd2SiO5 to the (Lu0.3Gd0.7)2SiO5 compositions, together with the enhancement of the structural and morphological characteristics, the scientific interest was centered in a designed doping strategy considering the most suitable rare earth ions (RE = Nd, Y and Yb).

### *4.3.1 Yttrium-doped (LGSO:Y)*

Yttrium was selected as a dopant, since it promotes an excellent thermal and optical properties [47], being usually introduced in oxide form as a stabilizing agent. In fact, it has been largely employed in laser materials, namely yttrium aluminum garnets (YAG) or thermal barrier coatings (TBCs) due to its good thermal conductivity (13.6 W m<sup>−</sup><sup>1</sup> K<sup>−</sup><sup>1</sup> ), shock resistance and low thermal expansion coefficient [64–66]. Additionally, its melting point (2425°C) is close to the one of Gd2O3 (2430°C).


*The conventional agreement indices Rexp, Rp and Rwp correspond to the expected, profile and weighted profile R-factors, respectively. The GOF parameter represents the goodness of fit.*

**91**

**Figure 9.**

*Crystal photograph and transmission spectrum of LGSO:Y [47].*

*Laser Floating Zone: General Overview Focusing on the Oxyorthosilicates Growth*

formation and maintaining the C2/c monoclinic structure.

*4.3.2 Neodyminum (LGSO:Nd) and ytterbium-doped (LGSO:Yb)*

The introduction of yttrium should bring stress hampering, maintaining the role of a laser passive element, by substitution of Lu3+ ions due to their similar atomic radius (212 pm for Y3+ and 217 pm for Lu3+) and considering that Y2SiO5 has C2/c monoclinic structure. Thus, the introduction of 5 mol% of yttrium provoked a significant increase on transparency, with transmittance values around 86% along the visible range, and also reducing or even avoiding crack formation when compared with the pure LGSO (**Figure 8**). As additional advantage, the relative absorption intensity of the charge transfer bands of the Gd3+ ions, namely the intra 4f <sup>7</sup> transitions, has been significantly increased (**Figure 9**), enhancing their suitability

On the other side, the introduction of yttrium does not bring significant modifications in the lattice structure of the crystal, since XRD powder diffractogram of the LGSO:Y totally matches with the 00-061-0488 ICDD XRD card like the LGSO-3 single crystal fiber [54], and the Rietveld refinement shows similar unit cell parameters for both materials (**Table 2**). Indeed, Y3+ ions have substituted Gd3+ ions due to their close ionic radii (0.90 Å and 0.94 Å in a 6-fold coordination, respectively) along with similar electronegativity values (1.22 and 1.20, respectively) [67]. Concomitantly, Y3+ has increased plasticity, thus reducing stress, minimizing crack

It should be noted that the approach presented here is in production process. Following the doping strategy for the (Lu0.3Gd0.7)2SiO5 (LGSO-3) matrix, the next step was the doping with laser active elements such as Nd3+ and Yb3+ aiming to produce laser active materials. These dopants are extensively used as emitting ions in several laser materials [4–6, 33, 34] produced by different crystallization methods. Indeed, de la Fuente et al. [33] and Black et al. [34] produced GdNdSiO5 and 7Gd2O3•9SiO2:Nd single crystal laser materials by LFZ in Ar:O2 atmospheres 30 years ago. However, most researchers employed standard growth methods. For example, Xu et al. [5] produced a controllable dual-wavelength continuous-wave laser emitting at 1075 and 1079 nm achieving an optical-to-optical efficiency of 63.3% for a Nd:Lu2SiO5 crystal grown by CZ, in which a peak power of 2.34 kW was measured under passively Q-switched operation. On the other side, Kim

*DOI: http://dx.doi.org/10.5772/intechopen.90309*

as matrix [47].

#### **Table 2.**

*Refined unit cell parameters and relative densities of GSO and lutetium and yttrium-doped single crystals calculated from XRD analysis in powders [18, 46, 47].*

*Laser Floating Zone: General Overview Focusing on the Oxyorthosilicates Growth DOI: http://dx.doi.org/10.5772/intechopen.90309*

The introduction of yttrium should bring stress hampering, maintaining the role of a laser passive element, by substitution of Lu3+ ions due to their similar atomic radius (212 pm for Y3+ and 217 pm for Lu3+) and considering that Y2SiO5 has C2/c monoclinic structure. Thus, the introduction of 5 mol% of yttrium provoked a significant increase on transparency, with transmittance values around 86% along the visible range, and also reducing or even avoiding crack formation when compared with the pure LGSO (**Figure 8**). As additional advantage, the relative absorption intensity of the charge transfer bands of the Gd3+ ions, namely the intra 4f <sup>7</sup> transitions, has been significantly increased (**Figure 9**), enhancing their suitability as matrix [47].

On the other side, the introduction of yttrium does not bring significant modifications in the lattice structure of the crystal, since XRD powder diffractogram of the LGSO:Y totally matches with the 00-061-0488 ICDD XRD card like the LGSO-3 single crystal fiber [54], and the Rietveld refinement shows similar unit cell parameters for both materials (**Table 2**). Indeed, Y3+ ions have substituted Gd3+ ions due to their close ionic radii (0.90 Å and 0.94 Å in a 6-fold coordination, respectively) along with similar electronegativity values (1.22 and 1.20, respectively) [67]. Concomitantly, Y3+ has increased plasticity, thus reducing stress, minimizing crack formation and maintaining the C2/c monoclinic structure.

#### *4.3.2 Neodyminum (LGSO:Nd) and ytterbium-doped (LGSO:Yb)*

It should be noted that the approach presented here is in production process. Following the doping strategy for the (Lu0.3Gd0.7)2SiO5 (LGSO-3) matrix, the next step was the doping with laser active elements such as Nd3+ and Yb3+ aiming to produce laser active materials. These dopants are extensively used as emitting ions in several laser materials [4–6, 33, 34] produced by different crystallization methods. Indeed, de la Fuente et al. [33] and Black et al. [34] produced GdNdSiO5 and 7Gd2O3•9SiO2:Nd single crystal laser materials by LFZ in Ar:O2 atmospheres 30 years ago. However, most researchers employed standard growth methods. For example, Xu et al. [5] produced a controllable dual-wavelength continuous-wave laser emitting at 1075 and 1079 nm achieving an optical-to-optical efficiency of 63.3% for a Nd:Lu2SiO5 crystal grown by CZ, in which a peak power of 2.34 kW was measured under passively Q-switched operation. On the other side, Kim

**Figure 9.** *Crystal photograph and transmission spectrum of LGSO:Y [47].*

*Synthesis Methods and Crystallization*

(RE = Nd, Y and Yb).

(13.6 W m<sup>−</sup><sup>1</sup>

**Crystal Rexp**

*4.3.1 Yttrium-doped (LGSO:Y)*

K<sup>−</sup><sup>1</sup>

**(%)**

**Rp (%)**

*respectively. The GOF parameter represents the goodness of fit.*

*calculated from XRD analysis in powders [18, 46, 47].*

**Rwp (%)**

lattice present both lutetium ions, and therefore, the LuO6 (Lu1) and LuO7 (Lu2) polyhedrons present the Cs local symmetry. The former has only one plane of symmetry, while the C3v point group presents higher steric effect. Additionally, despite the smaller ionic radius of the Lu3+, its inclusion into the monoclinic P21/c unit cell strongly affects the crystalline structure. Concomitantly, the GSO structure type allows low Lu doping. In opposite, the C2/c type structure presents minor steric effect and higher symmetry degrees of freedom, allowing the introduction of large size ions such as Gd3+ or Ce3+ on the Lu sites. Consequently, LGSO-3 and LGSO-5 samples have the C2/c crystalline structure, which is larger in size than P21/c (**Table 2**). On the other hand, **Table 2** shows how introduction of Lu decreases the volume of the cell together with an increase of the density. Concerning Raman spectroscopy characterization, LGSO-3 sample presents an intermediate spectrum between the GSO and LSO (**Figure 5**). In fact, when (ν1 + ν3) region is revised, LGSO-1 relates to A-type, like GSO structure, while LGSO-3 and LGSO-5 spectrum shape shows the typical doublet of B-type silicates, such as undoped LSO. Finally, the transmission studies of LGSO samples allow concluding that the Gd3+ ions are optically active. In fact, an

intra-ionic absorption due to the energy transfer band ascribed to 8

is observed, and this band is the highest for LGSO-3 sample, the one that is the most transparent and presents lower cracks. All these considerations allow to consider the LGSO-3 fibers as the most suitable host material for photonic applications [46].

**4.3 Rare-earth-doped lutetium and gadolinium oxyorthosilicates (LGSO:RE)**

Once the best laser host properties were determined by developing the initial Gd2SiO5 to the (Lu0.3Gd0.7)2SiO5 compositions, together with the enhancement of the structural and morphological characteristics, the scientific interest was centered in a designed doping strategy considering the most suitable rare earth ions

Yttrium was selected as a dopant, since it promotes an excellent thermal and optical properties [47], being usually introduced in oxide form as a stabilizing agent. In fact, it has been largely employed in laser materials, namely yttrium aluminum garnets (YAG) or thermal barrier coatings (TBCs) due to its good thermal conductivity

GSO 2.82 4.23 5.70 2.08 9.128 7.058 6.746 414.26 6.775 LGSO1 2.56 2.68 3.39 1.26 9.123 7.021 6.738 411.69 6.954 LGSO3 3.33 3.75 5.29 1.59 14.461 6.750 10.495 867.06 6.570 LGSOY 2.22 3.05 4.07 1.83 14.457 6.749 10.491 866.32 6.576 LGSO5 3.29 4.23 5.51 1.68 14.391 6.716 10.425 852.72 6.949 *The conventional agreement indices Rexp, Rp and Rwp correspond to the expected, profile and weighted profile R-factors,* 

*Refined unit cell parameters and relative densities of GSO and lutetium and yttrium-doped single crystals* 

Additionally, its melting point (2425°C) is close to the one of Gd2O3 (2430°C).

), shock resistance and low thermal expansion coefficient [64–66].

**GOF a (Å) b (Å) c (Å) Volume** 

S7/2 → 6

**(106 pm3 )**

**Density (g cm<sup>−</sup><sup>3</sup> )**

IJ transition

**90**

**Table 2.**

et al. [6] produced by hot-pressing a 10% Yb:Lu2O3 laser crystal pumped at 975 nm and emitting at 1080 nm presenting a slope efficiency of 74% with an output power of 16 W.

Considering the previous results of LGSO-3 samples, new powder mixtures were prepared by doping with 5 mol% of Nd2O3 and Yb2O3, using highly pure (5 N) oxide powders. Thus, neodymium (LGSO:Nd) and ytterbium (LGSO:Yb) doped LGSO single crystal fibers were produced by LFZ in air at 10 mm h<sup>−</sup><sup>1</sup> . However, these crystals present lower optical quality than those of LGSO doped with yttrium. The absorption of the LGSO:Yb crystals checked in a Z-cavity varied between 35 and 50% for a pumping of 978 nm Ti-sapphire laser, emitting at ~1039 nm wavelength (**Figure 10a**). On the other hand, LGSO:Nd diode pumped at 811 nm emits at ~1076 nm wavelength and absorbs 80% (**Figure 10b**).

#### **4.4 Lutetium oxyorthosilicate (LSO)**

Lutetium oxyorthosilicate (Lu2SiO5, LSO) has attracted the attention of researchers due to their favorable thermal and optical properties, which make it suitable as host materials to be used in photonics as laser media [3–6] or scintillators [7, 41, 59]. The main technique for producing LSO crystals is usually the CZ method. As an alternative, Farhi et al. [68] in 2008 grew by laser-heated pedestal growth (LHPG) rods of LSO and LSO:Ce3+ in air and N2 atmosphere at 15 mm h−<sup>1</sup> from square feed rods cut from a LSO pellet prepared by solid state reaction. Thus, it was expected that these type of oxyorthosilicates could be produced in air at 10 mm h<sup>−</sup><sup>1</sup> like the GSO. However, despite the fibers grown at 200 and 100 mm h<sup>−</sup><sup>1</sup> by the LFZ technique present a translucent aspect, the fibers obtained at lower pulling rates (10 and 5 mm h<sup>−</sup><sup>1</sup> ) are white and opaque (insets of **Figure 11**) [45]. SEM and EDS analysis of the samples produced by LFZ put in evidence a transition from single crystal to eutectic ceramics with the gradual appearance of the Lu2O3 phase into the Lu2SiO5 matrix as pulling rate is decreased. The eutectics present a banded structure of alternated monophasic oxyorthosilicate regions with a biphasic Lu2SiO5/Lu2O3 phases. The presence of both phases was also corroborated by XRD analysis [45].

The strong difference between the melting points of both precursors, SiO2 (1710°C) and Lu2O3 (2490°C), explains this behavior. In fact, the high laser power necessary to melt lutetium oxide induces SiO2 evaporation, by overheating during laser processing. This phenomenon was already observed by Farhi et al. [68]. The most volatile compounds tend to evaporate due to overheating when two materials

**93**

**Figure 12.**

**Figure 11.**

*(c) 10 mm h<sup>−</sup><sup>1</sup>*

 *and (d) 5 mm h<sup>−</sup><sup>1</sup>*

*phase diagram based on Yb2O3-SiO2 system [45, 69].*

*Laser Floating Zone: General Overview Focusing on the Oxyorthosilicates Growth*

*SEM micrographs and photographs of LSO samples grown by LFZ at (a) 200 mm h<sup>−</sup><sup>1</sup>*

 *[45].*

*, (b) 100 mm h<sup>−</sup><sup>1</sup>*

*,* 

with a great melting point mismatch are processed by LFZ. Concomitantly, a deviation from the nominal composition is observed, and consequently, the as-grown material exhibits a different composition. This is what happened in the Lu2O3-SiO2 system. Consequently, the crystallization path may vary, and therefore, the nature

*Compositional deviation from the nominal 1:1 composition to eutectic point (red dot) into the Lu2O3-SiO2*

*DOI: http://dx.doi.org/10.5772/intechopen.90309*

**Figure 10.** *Emitting wavelength of (a) LGSO:Yb and (b) LGSO:Nd crystals.*

*Laser Floating Zone: General Overview Focusing on the Oxyorthosilicates Growth DOI: http://dx.doi.org/10.5772/intechopen.90309*

#### **Figure 11.**

*Synthesis Methods and Crystallization*

output power of 16 W.

10 mm h<sup>−</sup><sup>1</sup>

analysis [45].

et al. [6] produced by hot-pressing a 10% Yb:Lu2O3 laser crystal pumped at 975 nm and emitting at 1080 nm presenting a slope efficiency of 74% with an

single crystal fibers were produced by LFZ in air at 10 mm h<sup>−</sup><sup>1</sup>

~1076 nm wavelength and absorbs 80% (**Figure 10b**).

**4.4 Lutetium oxyorthosilicate (LSO)**

pulling rates (10 and 5 mm h<sup>−</sup><sup>1</sup>

Considering the previous results of LGSO-3 samples, new powder mixtures were prepared by doping with 5 mol% of Nd2O3 and Yb2O3, using highly pure (5 N) oxide powders. Thus, neodymium (LGSO:Nd) and ytterbium (LGSO:Yb) doped LGSO

crystals present lower optical quality than those of LGSO doped with yttrium. The absorption of the LGSO:Yb crystals checked in a Z-cavity varied between 35 and 50% for a pumping of 978 nm Ti-sapphire laser, emitting at ~1039 nm wavelength (**Figure 10a**). On the other hand, LGSO:Nd diode pumped at 811 nm emits at

Lutetium oxyorthosilicate (Lu2SiO5, LSO) has attracted the attention of researchers due to their favorable thermal and optical properties, which make it suitable as host materials to be used in photonics as laser media [3–6] or scintillators [7, 41, 59]. The main technique for producing LSO crystals is usually the CZ method. As an alternative, Farhi et al. [68] in 2008 grew by laser-heated pedestal growth (LHPG) rods of LSO and LSO:Ce3+ in air and N2 atmosphere at 15 mm h−<sup>1</sup> from square feed rods cut from a LSO pellet prepared by solid state reaction. Thus, it was expected that these type of oxyorthosilicates could be produced in air at

by the LFZ technique present a translucent aspect, the fibers obtained at lower

SEM and EDS analysis of the samples produced by LFZ put in evidence a transition from single crystal to eutectic ceramics with the gradual appearance of the Lu2O3 phase into the Lu2SiO5 matrix as pulling rate is decreased. The eutectics present a banded structure of alternated monophasic oxyorthosilicate regions with a biphasic Lu2SiO5/Lu2O3 phases. The presence of both phases was also corroborated by XRD

The strong difference between the melting points of both precursors, SiO2 (1710°C) and Lu2O3 (2490°C), explains this behavior. In fact, the high laser power necessary to melt lutetium oxide induces SiO2 evaporation, by overheating during laser processing. This phenomenon was already observed by Farhi et al. [68]. The most volatile compounds tend to evaporate due to overheating when two materials

like the GSO. However, despite the fibers grown at 200 and 100 mm h<sup>−</sup><sup>1</sup>

) are white and opaque (insets of **Figure 11**) [45].

. However, these

**92**

**Figure 10.**

*Emitting wavelength of (a) LGSO:Yb and (b) LGSO:Nd crystals.*

*SEM micrographs and photographs of LSO samples grown by LFZ at (a) 200 mm h<sup>−</sup><sup>1</sup> , (b) 100 mm h<sup>−</sup><sup>1</sup> , (c) 10 mm h<sup>−</sup><sup>1</sup> and (d) 5 mm h<sup>−</sup><sup>1</sup> [45].*

#### **Figure 12.**

*Compositional deviation from the nominal 1:1 composition to eutectic point (red dot) into the Lu2O3-SiO2 phase diagram based on Yb2O3-SiO2 system [45, 69].*

with a great melting point mismatch are processed by LFZ. Concomitantly, a deviation from the nominal composition is observed, and consequently, the as-grown material exhibits a different composition. This is what happened in the Lu2O3-SiO2 system. Consequently, the crystallization path may vary, and therefore, the nature

and amount of solidified phases present in the crystallized material can be different. **Figure 12** puts in evidence the compositional deviation from the nominal composition (Lu2O3:SiO2 = 1:1) toward the eutectic point in the Lu2O3-SiO2 binary phase diagram (red dot). This compositional shift corroborates the SEM images of **Figure 11**, where an almost complete eutectic morphology is achieved in the slower processed fibers, the ones submitted to higher power for longer times. It is noteworthy the preferential alignment of the eutectic constituent, triggered by the strong axial thermal gradients at the solidification interface [70, 71]. The introduction of other rare earth ions such as Nd, with an intermediate melting point (2233°C), contributes to the decrease of the evaporation process, since both Lu2O3 lamellae presence inside the Lu2SiO5 and their size are reduced in diameter and significantly decreased in number.

Another interesting characteristic of the LSO fibers grown by the LFZ process is a pronounced photochromic effect, from white to pink-reddish tone. This behavior was observed in samples grown at lower pulling rates when irradiated with UV light. This effect persists for samples stored in the dark, even in the presence of oxidant atmosphere, while the bleaching of the photochromic coloration is reversible when samples are under natural illumination (**Figure 13**) [45].

## **4.5 Neodymium oxyorthosilicate (NSO)**

The Nd2SiO5 compound has been obtained only by solid state methods and, in the most cases, accompanied by other silicate phases, namely the pyrosilicate Nd2Si2O7 [72–74]. In fact, it must be noted that the production of this kind of orthosilicates is hard since the Nd2O3-SiO2 system melts incongruently [73]. Concomitantly, Jiang et al. [74] have recently sintered for microwave device applications, pure Nd2SiO5 starting from Nd2O3:SiO2 = 1:1.05 mixtures. A minimum deviation from this ratio promotes the formation of by-products such as Nd4Si3O12 or Nd2O3.

The processing of stoichiometric mixtures of SiO2 and Nd2O3 oxides through the LFZ technique produced large violet fibers. The apparent crystalline aspect of these fibers increases with pulling rate from umber-like (5 and 10 mm h<sup>−</sup><sup>1</sup> ) to brighter materials (100–400 mm h<sup>−</sup><sup>1</sup> ) (**Figure 14a**). The XRD analysis identified the presence of two phases, which were confirmed by SEM analysis as elongated Nd2SiO5 crystals inside of the Nd9.33(SiO4)6O2 matrix (**Figure 14b**). The phases present a preferential orientation along the fiber axis. Furthermore, the amount of each phase significantly depends on the pulling rate. Lower pulling rates tend to increase the nonstoichiometric phase, Nd9.33(SiO4)6O2.

**95**

*Laser Floating Zone: General Overview Focusing on the Oxyorthosilicates Growth*

Envisaging the applications of NSO fiber and considering the opposite electrical behavior of both phases together with the fibers texturing, mainly the ones

Hz. An increase of the AC conductivity with frequency and

at room temperature increases to 10<sup>−</sup><sup>2</sup>

their electrical properties. This way, the electrical conductivity and the dielectric constant were measured from room temperature until 1000°C and varying the fre-

temperature was observed for all samples. Specifically, at 1000°C and 10 Hz, the

The NSO fibers exhibit a typical response of ionic conductors [30, 71] with a p-type electronic behavior, according to León-Reina et al. [75] for Nd2SiO5 samples. On the other side, the dielectric constant decreases with frequency while an increase with temperature is observed. Values of 10 at room temperature increase up to 109 at 1000°C. The high densification degree of fibers and the different polarization mechanisms, as reported Jiang et al. [74], underlie this behavior. This consideration agrees with the typical characteristics of LFZ method that is known to produce samples with a higher density when compared with standard solid state sintering [76]. Additionally, these results confirm local variations in the Nd phases leading to

This chapter puts in evidence several advantages of the LFZ technique with respect to standard growth methods. In fact, LFZ is a suitable crystallization technique that allows obtaining highly oriented refractory materials such as the rare earth oxyorthosilicates. Focusing on the special characteristics of the LFZ process and extrapolating to other hard-synthesis materials, the LFZ revealed to be a suitable method for prototyping. This consideration is based on the capabilities that directly promote a reduction of the effective production costs, namely: it is a crucible-free technique, avoiding external contamination; it allows working with low precursors amount, together with the possibility to produce low volume of high-quality materials; it is a fast processing technique that allows reducing processing time; it allows the production of small-in-size high-quality single crystal or highly textured ceramics with an appropriate geometry, allowing the development of compact and miniaturized photonic devices; it allows the growth of directionally solidified eutectic ceramic materials; it allows the crystallization of metastable phases. Thus, it was demonstrated the ability to produce high-quality single crystals

S cm<sup>−</sup><sup>1</sup>

interstitial oxygen variations affecting the electrical response [75, 77].

), it is important to study

 *(NSO-400), and (b) SEM* 

 S cm<sup>−</sup><sup>1</sup> .

grown at the highest pulling rate (200 and 400 mm h<sup>−</sup><sup>1</sup>

*(a) Photographs of NSO samples grown at 10 (NSO-10) and 400 mm h<sup>−</sup><sup>1</sup>*

to 106

*micrograph identifying phases present in the NSO fiber.*

electrical conductivity of 10<sup>−</sup><sup>5</sup>

quency from 102

**Figure 14.**

**5. Conclusions**

*DOI: http://dx.doi.org/10.5772/intechopen.90309*

**Figure 13.**

*Photographs of parallel-polished LSO fibers showing photochromic effect after irradiation with UV light (254 nm) [45].*

*Laser Floating Zone: General Overview Focusing on the Oxyorthosilicates Growth DOI: http://dx.doi.org/10.5772/intechopen.90309*

**Figure 14.**

*Synthesis Methods and Crystallization*

decreased in number.

Nd4Si3O12 or Nd2O3.

materials (100–400 mm h<sup>−</sup><sup>1</sup>

the nonstoichiometric phase, Nd9.33(SiO4)6O2.

and amount of solidified phases present in the crystallized material can be different. **Figure 12** puts in evidence the compositional deviation from the nominal composition (Lu2O3:SiO2 = 1:1) toward the eutectic point in the Lu2O3-SiO2 binary phase diagram (red dot). This compositional shift corroborates the SEM images of **Figure 11**, where an almost complete eutectic morphology is achieved in the slower processed fibers, the ones submitted to higher power for longer times. It is noteworthy the preferential alignment of the eutectic constituent, triggered by the strong axial thermal gradients at the solidification interface [70, 71]. The introduction of other rare earth ions such as Nd, with an intermediate melting point (2233°C), contributes to the decrease of the evaporation process, since both Lu2O3 lamellae presence inside the Lu2SiO5 and their size are reduced in diameter and significantly

Another interesting characteristic of the LSO fibers grown by the LFZ process is a pronounced photochromic effect, from white to pink-reddish tone. This behavior was observed in samples grown at lower pulling rates when irradiated with UV light. This effect persists for samples stored in the dark, even in the presence of oxidant atmosphere, while the bleaching of the photochromic coloration is revers-

The Nd2SiO5 compound has been obtained only by solid state methods and, in the most cases, accompanied by other silicate phases, namely the pyrosilicate Nd2Si2O7 [72–74]. In fact, it must be noted that the production of this kind of orthosilicates is hard since the Nd2O3-SiO2 system melts incongruently [73]. Concomitantly, Jiang et al. [74] have recently sintered for microwave device applications, pure Nd2SiO5 starting from Nd2O3:SiO2 = 1:1.05 mixtures. A minimum deviation from this ratio promotes the formation of by-products such as

The processing of stoichiometric mixtures of SiO2 and Nd2O3 oxides through the LFZ technique produced large violet fibers. The apparent crystalline aspect of these

ence of two phases, which were confirmed by SEM analysis as elongated Nd2SiO5 crystals inside of the Nd9.33(SiO4)6O2 matrix (**Figure 14b**). The phases present a preferential orientation along the fiber axis. Furthermore, the amount of each phase significantly depends on the pulling rate. Lower pulling rates tend to increase

*Photographs of parallel-polished LSO fibers showing photochromic effect after irradiation with UV light* 

) (**Figure 14a**). The XRD analysis identified the pres-

) to brighter

ible when samples are under natural illumination (**Figure 13**) [45].

fibers increases with pulling rate from umber-like (5 and 10 mm h<sup>−</sup><sup>1</sup>

**4.5 Neodymium oxyorthosilicate (NSO)**

**94**

**Figure 13.**

*(254 nm) [45].*

*(a) Photographs of NSO samples grown at 10 (NSO-10) and 400 mm h<sup>−</sup><sup>1</sup> (NSO-400), and (b) SEM micrograph identifying phases present in the NSO fiber.*

Envisaging the applications of NSO fiber and considering the opposite electrical behavior of both phases together with the fibers texturing, mainly the ones grown at the highest pulling rate (200 and 400 mm h<sup>−</sup><sup>1</sup> ), it is important to study their electrical properties. This way, the electrical conductivity and the dielectric constant were measured from room temperature until 1000°C and varying the frequency from 102 to 106 Hz. An increase of the AC conductivity with frequency and temperature was observed for all samples. Specifically, at 1000°C and 10 Hz, the electrical conductivity of 10<sup>−</sup><sup>5</sup> S cm<sup>−</sup><sup>1</sup> at room temperature increases to 10<sup>−</sup><sup>2</sup> S cm<sup>−</sup><sup>1</sup> . The NSO fibers exhibit a typical response of ionic conductors [30, 71] with a p-type electronic behavior, according to León-Reina et al. [75] for Nd2SiO5 samples. On the other side, the dielectric constant decreases with frequency while an increase with temperature is observed. Values of 10 at room temperature increase up to 109 at 1000°C. The high densification degree of fibers and the different polarization mechanisms, as reported Jiang et al. [74], underlie this behavior. This consideration agrees with the typical characteristics of LFZ method that is known to produce samples with a higher density when compared with standard solid state sintering [76]. Additionally, these results confirm local variations in the Nd phases leading to interstitial oxygen variations affecting the electrical response [75, 77].

#### **5. Conclusions**

This chapter puts in evidence several advantages of the LFZ technique with respect to standard growth methods. In fact, LFZ is a suitable crystallization technique that allows obtaining highly oriented refractory materials such as the rare earth oxyorthosilicates. Focusing on the special characteristics of the LFZ process and extrapolating to other hard-synthesis materials, the LFZ revealed to be a suitable method for prototyping. This consideration is based on the capabilities that directly promote a reduction of the effective production costs, namely: it is a crucible-free technique, avoiding external contamination; it allows working with low precursors amount, together with the possibility to produce low volume of high-quality materials; it is a fast processing technique that allows reducing processing time; it allows the production of small-in-size high-quality single crystal or highly textured ceramics with an appropriate geometry, allowing the development of compact and miniaturized photonic devices; it allows the growth of directionally solidified eutectic ceramic materials; it allows the crystallization of metastable phases. Thus, it was demonstrated the ability to produce high-quality single crystals of the (Lu0.3Gd0.7)2SiO5 based composition in air at fast pulling rates. These crystals are suitable as laser passive and gain media. On the other side, Lu2O3/Lu2SiO5 eutectic ceramics exhibit an interesting reversible photochromic effect. Last, biphasic ceramics of Nd2SiO5/Nd9.33(SiO4)6O2 suitable for microwave devices can also be synthesized by the LFZ method.
