Synthesis, Luminescence and Magnetic Properties of Novel Fe 0.5 Gd 0.5 (MoO 4 ) 1.5 :Eu 3+ Micro/Nano (3D) Structures

The controlled synthesis of Fe 0.5 Gd 0.5 (MoO 4 ) 1.5 :Eu 3+ microcrystals (self-aggregated 3D su‐ perstructures) using hydrothermal method by employing PVP as surfactant along with the state of the art of this field at present. By varying the reaction time, we have reported the morphology selection and the condition to derive novel nanoparticle sheathed bipyr‐ amid-like morphology. The rest of the parameters like, molar ratio between initial precur‐ sor / surfactant and temperature were kept as constant. The Fe 0.5 Gd 0.5 (MoO 4 ) 1.5 :Eu 3+ microcrystals are found to be an excellent matrix for photoluminescence property and the Eu 3+ ion serves as a good red emitting luminescent center. Further, room temperature (RT) magnetic properties of Fe 0.5 Gd 0.5 (MoO 4 ) 1.5 :Eu 3+ were investigated in detail. mechanism for the formation of microstructures clearly involves the layer-by-layer self-assembly of 2D nanoflakes with successive disassembly, via an Ostwald ripening phenomena. The photoluminescence emission properties of Eu 3+ doped Fe 0.5 Gd 0.5 (MoO 4 ) 1.5 were investigat‐ ed. Under the excitation of 395 nm UV light, the as-synthesized samples show red emission from the hypersensitive 5 D 0 → 7 F 2 transition at 615 nm. RT magnetic properties of the nanopar‐ ticles sheathed porous bipyramid-like Fe 0.5 Gd 0.5 (MoO 4 ) 1.5 :Eu 3+ structures clearly exhibit the paramagnetic behavior due to the presence of paramagnetic Gd 3+ ions. The current experi‐ mental results are important and may open up a new scope for the design and formulation of bifunctional magnetic and luminescence applications.


Introduction
Size-and shape-controlled synthesis of self-organized, three-dimensional (3D) micro/nano architectures are still challenging and much attracted in the recent years owing to vast scientific and technological interest in multifaceted research areas [11,27,14]. The growth and development of uniform, self-aggregated 3D super-structures through plane-to-plane coalition of the basic building blocks have been paid significant attention owing to their unusual physical, chemical properties [29,3]. The development of self-organized architectures consents to find neoteric and diversified materials, causing momentous discovery that has been developed for the construction of a new class of micro/nanostructured devices [14,15]. Self-aggregation of hierarchical architectures has proved to be a virtuous and expedient tool to control the structure and properties for the fabrication of intricate networks [15]. The peculiar size and morphology of the self-assembled 3D networks determine the attributes of a material which are important for the manufacture of a novel category of micro/nano-structured devices for advanced engineering and sciences [29,14,13]. The supreme and hopeful approach to synthesize self-assembled 3D networks is to use a solution-based technique which is a simple route to regulate the physicochemical properties of materials [3]. Specifically, in the hydrothermal method, numerous versatile morphologies have been described by using surfactants or chelating agents [7,16,17]. The surface capping agent used in the hydrothermal synthesis method positively assures an effective way to regulate the nucleation, controlled growth, oriented aggregation mechanism, and self-organized 3D morphology [15,4].

Recent research scenario
A wide variety of 3D super-structures can be synthesized by using a suitable amount of surfactant which reduces the particle-particle amalgamation by steric effects, thereby controlling the size and shape [15]. Up till now, a number of research works have been reported on controlled synthesis of 3D hierarchical architectures using hydrothermal technique, for example, bowknot-like Y 2 (WO 4 ) 3 :Ln 3+ [9], almond-like (Na 0.5 La 0.5 )MoO 4 :RE 3+ [14], monodisperse CaMoO 4 :Eu 3+ , M + (M = Li, Na, K) microspheres [18], micron-sized flower-like NaCe(MoO 4 ) 2 architectures [27], tetragonal bipyramid-like (Na 0.5 Gd 0.5 )MoO 4 :Ln 3+ [15], rugbylike NaEu(MoO 4 ) 2 microstructures [26], sheaf-like Gd 2 (MoO 4 ) 3 [24], etc. Large-scale assert for phosphor materials as efficient sources of energy that can supply sustained proficiency is growing gradually. Current research in phosphors is focused on new materials having both luminescence and magnetic properties in a single entity based on the presence of trivalent lanthanide ions (Ln 3+ ) with magnetic Fe 3+ ions. These bifunctional materials have attracted worldwide intense research, because their up/down conversion luminescence and para/ ferromagnetic properties are strongly required for therapeutics, contrast agents in magnetic resonance (MRI), fluorescent bioimaging in biophotonics, drug delivery and lumino-magnetic applications [6,13,19]. The phosphor particles can be magnetically directed, aligned, tracked, after applying the external magnetic fields. Subsequently, their luminescence can be visualized under optical excitation, which can be used widely for biological labeling, imaging of human and animal cells, tissues, and in vitro, in vivo applications [22,25]. The luminescence and magnetic properties of lanthanide ions doped iron-based inorganic compounds that are synthesized by different research groups are detailed as follows. The novel Fe 3 O 4 @YPO 4 :Re (Re = Tb, Eu) magnetic-fluorescent hybrid spheres were prepared using solvothermal and co-precipitation techniques [25]. The obtained nanostructures are an excellent platform to integrate fluorescent materials and magnetite into one single entity to exhibit both magnetic and fluorescent properties [25]. Wang et al. [25] reported that human cervical carcinoma Hela cells were successfully labeled by using the Fe 3 O 4 @YPO 4 :Re hybrid spheres. Zhang et al. [29] synthesized orthorhombic cubic GdFeO 3 particles by using a facile hydrothermal method. The emission color of cubic GdFeO 3 particles could be adjusted effectively by doping different lanthanide activators [29]. Also, cubic GdFeO 3 particles exhibiting paramagnetic properties are reported to be used as an excellent luminescence and magnetic material [29]. To replace the existing halide-based upconverting phosphors for infrared-based biomedical imaging [1], nontoxic Gd 2 O 2 S:Yb/Er is synthesized using flux fusion method. The synthesized phosphor not only enables near-IR imaging features but also at the same time could be used as a contrast agent in MRI imaging [1]. Multifunctional luminescentmagnetic YAG:Ce nano-phosphors were synthesized by post-heat solidified combustion technique, post-heated hydrothermal-homogenous precipitation, and post-heated auto-clave techniques, respectively, using inexpensive aluminum and yttrium nitrates as the starting materials and urea as the homogenizing precipitant [10]. Since the yttrium and aluminium are non-magnetic elements, the origin of ferromagnetism of these nonmagnetic oxides could be attributed solely to the defects and/or oxygen vacancies [10]. The novel YAG:Ce nanophosphor exhibits the ferromagnetic behavior which finds the way for a new class of magneto-optic and spintronic materials for a wide variety of applications. The multicolor upconversion emissions and paramagnetic nature were observed in β-NaGdF 4 crystals, which were synthesized by one-step precipitation method at room temperature [8]. To control the crystal size and morphology of the β-NaGdF 4 crystals, different types of surfactants, namely Na 2 EDTA, PVP, SDS, and Na 2 tar, were introduced during the synthesis procedure. Due to the presence of paramagnetic Gd 3+ ions, β-NaGdF 4 crystals exhibit paramagnetic behavior, which is a favorable bifunctional candidate for bioimaging applications [8].
Scheelite-type metal molybdates are considered as an ideal candidate, and are receiving accelerating interest due to their remarkable luminescence, magnetic, catalytic, sensing, and photocatalytic properties [13]. Scheelite-type crystalline structures, with the general chemical formula such as (Na 0.5 R 0.5 )MoO 4 :Ln 3+ [15,14] [14,15]. In the crystal structure of Fe 0.5 R 0.5 (MoO 4 ) 1.5 :Ln 3+ , trivalent Fe 3+ , R 3+ /Ln 3+ jointly occupy the dodecahedral positions and molybdenum (Mo 6+ ) atoms populated at the center of the tetrahedral symmetry coordinated with four equivalent oxygen atoms. Scheelite-type metal molybdates with the general formula have been synthesized by various techniques, which include hydrothermal method [14,15], solid-state reaction technique [12], hydrothermal-assisted solid-state reaction [28], and pulsed laser deposition technique [21]. The random distribution of R 3+ (La or Gd or Y) in the scheelite tetragonal structures show an intense and broad absorption band in the near UV-region [15].
Among all these molybdates, (Fe 0.5 Gd 0.5 )MoO 4 :Eu 3+ is an important opto-magnetic material and possess good luminescence property. Due to the notable emission spectral lines in Ln 3+ doped phosphors extending from ultraviolet to infra-red regionand its magnetic properties may open up a new platform to design and formulate other inorganic functional materials with for potential magnetic and luminescence applications [13], there is a great deal of scientific and technological interest in developing novel opto-electronic applications. In general, synthesis of any kind of phosphor materials using the conventional/sol-gel technique would require laborious conditions such as hefty manual grinding, annealing, or calcination of samples to high temperature, intermediate grinding process, and heat treatment for several times, etc. In order to avoid the above mentioned difficulties, hydrothermal technique is the alternative and most promising approach to synthesize the variety of phosphor materials with desired size, shape, and dimensions, crystallinity by changing the experimental parameters.
Herein, we report the controlled synthesis of (Fe 0. 5

Characterization
XRD pattern of as-synthesized phosphor was analyzed using PANalytical's X'Pert PRO materials research, X-ray diffractometer equipped with a Cu-Kα radiation (λ = 1.54060 A°) at a scanning rate of 0.02° s -1 performed in the range of 20-60 degrees. Morphology and energydispersive X-ray spectra (EDX) of the product were investigated by scanning electron microscope (FESEM (Quanta 3D FEG)). The spacing between the two adjacent lattice planes was measured using high-resolution transmission electron microscope (HRTEM JEOL 3010). Furthermore, the room-temperature (RT) photoluminescence studies were carried out using Horiba-Jobin Yvon Fluromax-4P bench-top Spectrofluorometer. Room-temperature magnetic properties of the samples were analyzed using (Lake Shore 7307 model) vibrating sample magnetometer (VSM).

Morphological investigations
To explore the 3D surface morphology, particle size distribution, and formation mechanism for the evolution of nanoparticle sheathed bipyramid-like structures, a series of time-dependent experiments were carried out using a PVP employed hydrothermal route. The FESEM and TEM analyses were used to characterize the morphology of the final products. By changing the experimental reaction time interval with fixed temperature (200°C), pH (~7), and molar concentration of the PVP (0.1 mM), a substantial difference was observed in the final product. Figure (1-3)shows the low, high magnifications FESEM image of the Fea 0.5 Gd 0.5 (MoO 4 ) 1.5 :Eu 3+ samples synthesized by hydrothermal route at different time intervals (1, 3, 6, 12, 24, and 48 h) with fixed temperature (200°C), pH (~7), and PVP molar concentration. During the initial period of 1 h time interval, numerous 2D nanoflakes with few tens of nanometer were observed, which acts as a primary building block for the subsequent growth of 3D microstructures (Figure 1 (a)). It was noticed from Figure 1 (b, c), when the hydrothermal time period was increased to 3 and 6 h, nanoflakes began to self-organize continuously through plane-to-plane coalition and try to form a bipyramidal morphology (average diameter of 1 μm). However, the morphology and size distribution was found to be less uniform. When the reaction time interval was kept at 12 h, bipyramid-like morphology with an average of 1.0 μm in length and an average of 1.2 μm in diameter was obtained and shown in Fig. 1 (d). When the reaction time period was raised to 24 h, highly ordered and self-assembled porous nanoparticle sheathed bipyramid-like morphology with the size approximately equal to ~1.2 μm diameter was observed (Figure 2 (a, b)). Further, increasing the reaction time to 48 h, the final product morphology consisted of irregular porous bipyramid-like structures in which nanoparticles are sheathed and shown in Figure 2 (c, d). This may be due to the prolonged time interval, resulting in thermal collision between the particles (growth stage; the self-assembly process predominates between these crystals because of its high surface energies) [14]. This involves growth from 0D primary particles to 2D nanosheets, followed by the formation of 3D hierarchical networks through an assembly-disassembly process [14]. The TEM image of the sample synthesized at 24 h time interval with 0.1 mM of PVP molar concentration is shown in Figure 3a and the corresponding inset shows the FFT pattern. The formation mechanism for the evolution of a nanoparticle-sheathed bipyramid-like Fe 0.5 Gd 0.5 (MoO 4 ) 1.5 :Eu 3+ structure can be described as follows. Primarily, smaller crystalline nuclei formed in a supersaturated solution starts the crystallization process for subsequent growth of self-organization. During the self-organization process, smaller nanocrystals were grown-up constantly to form bigger particles via an Ostwald ripening phenomenon at higher reaction time intervals, due to interactions between the amorphous nanoparticles, resulting in 2D nanoflakes [14]. Initially, PVP acts as a surface capping agent to form a stable complex with Gd 3+ /Fe 3+ and then kinetically controls the reaction rate, germination of nuclei, the growth rate, and the oriented aggregation mechanism. When the reaction temperature gradually increases to higher temperature, PVP would decompose gradually and has no obvious effect on the possible growth of nuclei. When the time period was increased, these 2D nanoflakes joined each other along a mutual crystallographic orientation through plane-to-plane conjunction of neighboring particles [14]. In general, such amalgamation process between the atoms/ions in molecules/crystals can induce dipole moments, which can be associated with certain specific crystallographic orientations [13]. The interaction among dipole moments in nearby nanoparticles is highly probable and acts as a driving factor for the oriented attachment procedure by allocation of a common crystallographic facet. The growth rate in Fe 0 Gd 0.5 (MoO 4 ) 1.5 :Eu 3+ crystals is oriented preferentially along the [001] direction. Donnay-Harker et al. [5] reported that, for tetragonal structures, the surface free energy of the [001] face is larger than that of the [101] face [5,2]. As a result, the faster growth rate in the  The as-grown 2D nanoflakes are continuously self-assembled via a layer-by-layer stacking process to form 3D bipyramid-like structures. Then, the completely developed bipyramid particles are readily disassembled into smaller nanoparticles, which are finally sheathed on individual bipyramid-like particles. After aging for a longer time period, the disassembly of well-organized structures could increase the entropy of the system and thus could decrease the free energy of the whole system [16], resulting in the nanoparticles arbitrarily sheathed on individual bipyramid-like particles. The assembly-disassembly process in Fe 0 Gd 0.5 (MoO 4 ) 1.5 :Eu 3+ was described in our previous work [13] by using EDTA as a surface capping agent.

Structural analysis
The chemical phase purity and crystalline nature of the product were investigated using X-ray diffraction patterns. Figure 5 shows the XRD pattern of Fe 0.5 Gd 0.5 (MoO 4 ) 1.5 :Eu 3+ samples synthesized by a facile hydrothermal route at different time intervals (6,12,24, and 48 h). All the peaks are perfectly matched with the standard JCPDS card no. 25-0828 of (Na 0.5 Gd 0.5 )MoO 4 . It could be clearly observed that the XRD patterns of as-synthesized samples are highly crystalline, and the strongest intensity peak is observed at 2θ = 28.67 degrees analogous to (112) plane. The XRD pattern reveals that they belong to a tetragonal phase corresponding to the scheelite structure with the space group I41/a. In this crystal structure Fe 3+ , Gd 3+ /Eu 3+ ions jointly occupy the dodecahedral sites of the tetrahedra. Molybdenum atoms (Mo 6+ ) populated in the center of tetrahedral symmetry is surrounded by four equivalent oxygen (O 2-) atoms [13] and forming isolated [MoO 4 ] 2-group. Owing to their similar ionic radius and valance state, the Eu 3+ ion successfully replaces the Gd 3+ ion and does not change the lattice site of the host Fe 0.5 Gd 0.5 (MoO 4 ) 1.5 :Eu 3+ and the crystal phase is very much pure. Further, no other extra peaks of impurity were observed. Figure 5 (a, b) shows the representative EDX analysis, taking single bipyramid-like particle and single nanoparticle sheathed on bipyramidal structure synthesized at 24 h time interval for Eu 3+ doped Fe 0.5 Gd 0.5 (MoO 4 ) 1.5 . The energy-dispersive X-ray spectrum was used to confirm the presence of iron (Fe 3+ ), gadolinium (Gd 3+ ), europium (Eu 3+ ), molybdenum (Mo 6+ ), and The chemical phase purity and crystalline nature of the product were investigated using Xray diffraction patterns. Figure 5 shows the XRD pattern of Fe0.5Gd0.5(MoO4)1.5:Eu 3+ samples synthesized by a facile hydrothermal route at different time intervals (6,12,24, and 48 h). All the peaks are perfectly matched with the standard JCPDS card no. 25-0828 of (Na0.5Gd0.5)MoO4. It could be clearly observed that the XRD patterns of as-synthesized samples are highly crystalline, and the strongest intensity peak is observed at 2θ = 28.67 degrees analogous to (112) plane. The XRD pattern reveals that they belong to a tetragonal phase corresponding to the scheelite structure with the space group I41/a. In this crystal structure Fe 3+ , Gd 3+ /Eu 3+ ions jointly occupy the dodecahedral sites of the tetrahedra. Molybdenum atoms (Mo 6+ ) populated in the center of tetrahedral symmetry is surrounded by four equivalent oxygen (O 2  ) atoms (Krishnan et al., 2015) and forming isolated [MoO4] 2  group. Owing to their similar ionic radius and valance state, the Eu 3+ ion successfully replaces the Gd 3+ ion and does not change the lattice site of the host Fe0.5Gd0.5(MoO4)1.5:Eu 3+ and the crystal phase is very much pure. Further, no other extra peaks of impurity were observed. Figure. 6 (a) EDX spectrum of single bipyramid-like Fe0.5Gd0.5(MoO4)1.5:Eu 3+ particle, (b) EDX spectrum of single nanoparticle sheathed on a bipyramid-like particle.  Upon 395 nm UV irradiation, the emission spectrum was governed by the hypersensitive red emission, showing a transition 5 D 0 → 7 F 2 (due to electric dipole transition) higher than 5 D 0 → 7 F 1 (magnetic dipole). In the emission spectrum, the transitions 5 D 0 → 7 F J (where J = 1, 2, 3, 4) were observed due to intra-configurational f-f electronic transitions of Eu 3+ ions. The presence of electric dipole transition confirmed that Eu 3+ ions were located at sites without inversion symmetry (C 3v symmetry). The other transitions 5 D 0 → 7 F 3 and 5 D 0 → 7 F 4 were comparatively very weak for all the samples (not shown in PL spectrum). However, the presence of magnetic iron (Fe 3+ ) in the Fe 0.5 Gd 0.5 (MoO 4 ) 1.5 tetragonal crystal structure considerably decreases their luminescence, as Fe 3+ ions share the dodecahedral sites with Gd 3+ /Eu 3+ [13]. However, it is still unclear for the weak red emission in Eu 3+ doped Fe 0.5 Gd 0.5 (MoO 4 ) 1.5 . Figure 8 shows the room-temperature (RT) magnetic properties of hierarchically self-organized Fe 0.5 Gd 0.5 (MoO 4 ) 1.5 :Eu 3+ 3D microstructures synthesized by the hydrothermal route at 24 h time interval. Magnetization as a function of applied magnetic field (from 15000 Oe to 15000 Oe) was measured using a vibrating sample magnetometer. Due to the presence of Gd 3+ ions, a magnetic hysteresis (M-H) loop was not observed in the case of Eu 3+ doped Fe 0.5 Gd 0.5 (MoO 4 ) 1.5 . From Figure 8, it is clear that a straight line crosses the origin, indicating that the phosphor Fe 0.5 Gd 0.5 (MoO 4 ) 1.5 :Eu 3+ exhibits a paramagnetic behavior due to the existence of paramagnetic Gd 3+ ions and the saturation magnetization (Ms) value is found to be 0.028 emu/gm for RT. The extremely localized nature of the seven unpaired inner 4f electrons of Gd plays an important role which determines its magnetic properties [15]. These unpaired electrons in the outer orbital are closely bound to the nucleus and effectively shielded by the outer closed shell electrons 5s 2 5p 6 from the crystal field [15]. Even though the Gd 3+ ions jointly occupy the dodecahedral sites with Fe 3+ ions, number of 4f electrons in the Gd 3+ ions, atomic unit cell volume, direct f-f exchange interactions between neighboring Gd 3+ and Fe 3+ atoms are responsible for setting up the magnetic moments [15,14]. Since, Gd 3+ ions have total orbital angular momentum L = 0 [13], the spin orbit coupling between the partially filled 4f electrons in the Gd 3+ and Fe 3+ ions is weak, which inhibits sufficient orbital overlaps [8].

Conclusion
In summary, the interaction between the Gd 3+ and Fe 3+ ions in the crystal structure Fe 0.5 Gd 0.5 (MoO 4 ) 1.5 :Eu 3+ is weak and hence insufficient overlap of the orbitals associated with 4f shells gives rise to paramagnetism. Further, more detailed investigations are required to determine the magnetic behavior of Fe 0.5 Gd 0.5 (MoO 4 ) 1.5 :Eu 3+ at various temperatures. The nanoparticle sheathed Fe 0.5 Gd 0.5 (MoO 4 ) 1.5 :Eu 3+ porous bipyramid-like structures were successfully synthesized using hydrothermal technique by employing PVP as the surfactant. The hydrothermal reaction time period was the key parameter and plays an important role for morphological evolution of self-aggregated 3D hierarchical networks. A possible growth mechanism for the formation of microstructures clearly involves the layer-by-layer selfassembly of 2D nanoflakes with successive disassembly, via an Ostwald ripening phenomena.