Funkcionális Nanostruktúrák Kutatócsoport https://wigner.hu/index.php/hu hu 2022_Functional Nanostructures Research Group https://wigner.hu/index.php/hu/node/2499 <span class="field field--name-title field--type-string field--label-hidden">2022_Functional Nanostructures Research Group</span> <div class="clearfix text-formatted field field--name-body field--type-text-with-summary field--label-hidden field__item"><h4><strong>2022</strong></h4> <p><strong>Laser-induced magnetism in FeRh thin film.</strong> — A laser-induced magnetic pattern was successfully generated in 109 nm thick Fe<sub>51</sub>Rh<sub>49 </sub>film deposited on an MgO (100) substrate. The initial, A1 structure with fully paramagnetic magnetic ordering was achieved after irradiating the samples with 120 keV Ne<sup>+</sup> ions with a fluence of 1 × 10<sup>16</sup> ion/cm2, as it was confirmed by conversion-electron Mössbauer spectroscopy and X-ray diffraction. The FeRh film was locally illuminated by a 730 nm laser beam with its power ranging from 20 mW to 200 mW. At higher powers we found that the beam ablated the film, but at 20 mW no sign of physical damage could be observed. In this lowest power case, magnetic force microscopy revealed a well-defined magnetic structure reflecting the laser irradiation pattern. We suggest that the great adaptability of the presented technique in FeRh thin films can contribute to develop cutting-edge spintronic applications.</p> <img alt="INYF" data-entity-type="file" data-entity-uuid="5fb8eb77-cb7a-4d6a-bf44-d18d1dbb309c" src="https://wigner.hu/sites/default/files/inline-images/INYF.png" width="800" class="align-center" /> <p><em>Fig. 2. (a) Magnetic force microscopy image of the sample before laser irradiation, (b) scanning probe microscopy tomography, (c) Magnetic force microscopy image image of the 20 mW laser illuminated sample and (d) Gaussian fit of the phase values of an arbitrary laser-induced magnetic spot</em></p> </div> <span class="field field--name-uid field--type-entity-reference field--label-hidden"><span lang="" about="https://wigner.hu/index.php/hu/user/124" typeof="schema:Person" property="schema:name" datatype="" xml:lang="">Pentek Csilla</span></span> <span class="field field--name-created field--type-created field--label-hidden">h, 02/13/2023 - 14:03</span> <div class="field field--name-field-ev field--type-datetime field--label-above"> <div class="field__label">Év</div> <div class="field__item"><time datetime="2023-02-13T12:00:00Z" class="datetime">h, 02/13/2023 - 12:00</time> </div> </div> Mon, 13 Feb 2023 13:03:00 +0000 Pentek Csilla 2499 at https://wigner.hu 2021_Functional Nanostructures https://wigner.hu/index.php/hu/node/2323 <span class="field field--name-title field--type-string field--label-hidden">2021_Functional Nanostructures</span> <div class="clearfix text-formatted field field--name-body field--type-text-with-summary field--label-hidden field__item"><h4><strong>2021</strong></h4> <p><strong>Synergy effect of temperature, electric- and magnetic field on the depth structure of the FeRh/BaTiO<sub>3</sub> composite multiferroic </strong>— FeRh based composite multiferroic materials have attracted great scientific interest due to their wide variety of possible applications in future nano device technology. In this work, a comprehensive study on the depth dependence of the metamagnetic phase transition in FeRh/BaTiO<sub>3</sub> heterostructure was investigated by means of single or combined external stimulus such as heat, magnetic or electric field. Grazing-incidence nuclear scattering experiments revealed significant discrepancies in the mechanism of the antiferromagnetic/ferromagnetic reordering induced by the different effects, with distinguished role of both upper and lower interfaces.</p> <img alt="FN1" data-entity-type="file" data-entity-uuid="f7aa1f7e-51ec-472f-b8c7-90dd31d63193" src="https://wigner.hu/sites/default/files/inline-images/FN1.png" width="600" class="align-center" /> <p><em>Figure 1. The variation of the antiferromagnetic ratio (X<sub>AFM</sub>) as a function of temperature with and without applying 30 V voltage on the FeRh/BaTiO<sub>3</sub> multiferroic system.</em></p> <p><strong>A Three-Dimensional Analysis of Magnetic Nanopattern Formation in FeRh Thin Films on MgO Substrates.</strong> — Magnetic nanopatterns were successfully created in [<sup>nat</sup>Fe<sub>51</sub>Rh<sub>49</sub>(63 Å)/<sup>57</sup>Fe<sub>51</sub>Rh<sub>49</sub>(46 Å)]<sub>10 </sub>isotope-periodic multilayer structures deposited on MgO (100) substrate. Silica and polystyrene spherical masks, nominally 500 nm and 1000 nm in diameter, respectively were applied on the surface of the sample in order to locally shadow the multilayers against the effect of 110 keV energy neon ion irradiation with fluences of 10<sup>15</sup> ion/cm<sup>2</sup> and 10<sup>16</sup> ion/cm<sup>2</sup>. Such nanosphere-lithography technique allows projecting the mask geometry on the magnetic structure of the FeRh film. Conversion-electron Mössbauer spectroscopy and magnetic force microscopy were used to determine the ferromagnetic ratio and the magnetic pattern in the samples, and nuclear resonance scattering of synchrotron radiation was applied to obtain the in-depth magnetic profile. From the results obtained, the possible 3D structure of the created individual magnetic domains was also constructed.</p> <img alt="FN2" data-entity-type="file" data-entity-uuid="8d330dab-cce5-4586-9596-f84530ab8b7a" src="https://wigner.hu/sites/default/files/inline-images/FN2.png" width="600" class="align-center" /> <p><em>Figure 2. Magnetic force microscopy image recorded on FeRh thin film irradiated through 1000 nm polystyrene spherical mask with 10<sup>16</sup> ion/cm<sup>2</sup> neo ions. By the evaluation of grazing incidence nuclear resonance scattering results, the 3-dimensional shape of the formed ferromagnetic domains (red color) could be constructed.</em></p> </div> <span class="field field--name-uid field--type-entity-reference field--label-hidden"><span lang="" about="https://wigner.hu/index.php/hu/user/124" typeof="schema:Person" property="schema:name" datatype="" xml:lang="">Pentek Csilla</span></span> <span class="field field--name-created field--type-created field--label-hidden">k, 08/30/2022 - 12:08</span> <div class="field field--name-field-ev field--type-datetime field--label-above"> <div class="field__label">Év</div> <div class="field__item"><time datetime="2022-08-30T12:00:00Z" class="datetime">k, 08/30/2022 - 12:00</time> </div> </div> Tue, 30 Aug 2022 10:08:47 +0000 Pentek Csilla 2323 at https://wigner.hu 2020_Functional nanostructures https://wigner.hu/index.php/hu/node/1714 <span class="field field--name-title field--type-string field--label-hidden">2020_Functional nanostructures</span> <div class="clearfix text-formatted field field--name-body field--type-text-with-summary field--label-hidden field__item"><h4><strong>2020</strong></h4> <p>Reversible control of magnetism in FeRh<a href="https://pubs.rsc.org/en/content/articlelanding/2020/CP/D0CP00465K#!divAbstract"> [1]</a>. — The multilayer of approximate structure MgO(100)/[<sup>n</sup>Fe<sub>51</sub>Rh<sub>49</sub>(63 Å)/<sup>57</sup>Fe<sub>51</sub>Rh<sub>49</sub>(46 Å)]<sub>10 </sub>deposited at 200 °C is primarily of paramagnetic A1 phase and is fully converted to the magnetic B2 phase by annealing at 300 °C for 60 min. Subsequent irradiation by 120 keV Ne<sup>+</sup> ions turns the thin film completely to the paramagnetic A1 phase. Repeated annealing at 300 °C for 60 min results in 100 % magnetic B2 phase, i.e. a process that can be repeated reversibly. The A1 <img alt="nyíl" data-entity-type="file" data-entity-uuid="4856a9e1-806b-4d3d-873b-009ebaec42b6" src="https://wigner.hu/sites/default/files/inline-images/nyil.png" width="20" />B2 transformation takes place without any plane-perpendicular diffusion while Ne<sup>+</sup> irradiation results in significant interlayer mixing.</p> <img alt="funkcionális nanostruktúrák 1" data-entity-type="file" data-entity-uuid="20b62b9a-6c8f-4815-b130-e6c14d8b5c3c" src="https://wigner.hu/sites/default/files/inline-images/funkcionalis_nano1.png" width="800" class="align-center" /> <p><em><strong>Figure 1.</strong> Conversion-electron Mössbauer spectroscopy (CEMS) spectra, high-angle X-ray diffraction (XRD), and unpolarized neutron reflectivity (NR) patterns recorded on the as-deposited MgO(100)/ [<sup><sub>n</sub></sup>FeRh/<sup>57</sup>FeRh]<sub>10</sub> sample, after annealing for 60 min at 300 °C, after subsequent irradiation by 120 keV Ne<sup>+</sup> ions, with a fluence of 1 × 10<sup>16 </sup>at/cm<sup>2</sup> and after subsequent annealing for 60 min at 300 °C.</em></p> <p><strong>Magnetic nanopattern in FeRh thin film.</strong> — FeRh binary alloy system has been extensively investigated due to its potential applications in novel magnetic as well as magnetocaloric devices. In this work we successfully created magnetic nanopattern in<br /> [<sup>n</sup>Fe<sub>51</sub>Rh<sub>49</sub> (63 Å)/<sup>57</sup>Fe<sub>51</sub>Rh<sub>49</sub>(46 Å)]<sub>10</sub> isotope periodic multilayer deposited on MgO (100) substrate. Nominally 500 nm and 1000 nm polystyrene spherical mask was applied on the surface of the sample to shadow the effect of 10<sup>15 </sup>ion/cm<sup>2 </sup>and 10<sup>16</sup> ion/cm<sup>2</sup>, 110 keV energy neon ion irradiation, hence project the mask geometry in the magnetic structure of FeRh film. Conversion electron Mössbauer spectroscopy and magnetic force microscopy were used to determine the ferromagnetic ratio and the magnetic pattern in the sample, and nuclear resonance scattering of synchrotron radiation to obtain the in-depth magnetic profile. From the results, we also constructed the 3D visualization of the created individual magnetic domains.</p> <img alt="funkcionális nanostruktúrák 2" data-entity-type="file" data-entity-uuid="98709973-e62c-4bb9-95d3-23c4b985ff58" src="https://wigner.hu/sites/default/files/inline-images/funkcionalis_nano2_0.png" width="400" class="align-center" /> <p><br /> <em><strong>Figure 2.</strong> Magnetic force microscopy image recorded on FeRh thin film after 10<sup>16</sup> ion/cm<sup>2</sup> irradiation through 1000 nm polystyrene mask. The dark regions represent the ferromagnetic domains of B2 structure embedded in a paramagnetic A1 matrix.</em></p> <p> </p> </div> <span class="field field--name-uid field--type-entity-reference field--label-hidden"><span lang="" about="https://wigner.hu/index.php/hu/user/124" typeof="schema:Person" property="schema:name" datatype="" xml:lang="">Pentek Csilla</span></span> <span class="field field--name-created field--type-created field--label-hidden">cs, 02/18/2021 - 09:07</span> <div class="field field--name-field-ev field--type-datetime field--label-above"> <div class="field__label">Év</div> <div class="field__item"><time datetime="2020-01-02T12:00:00Z" class="datetime">cs, 01/02/2020 - 12:00</time> </div> </div> Thu, 18 Feb 2021 08:07:46 +0000 Pentek Csilla 1714 at https://wigner.hu 2019_Functional nanostructures https://wigner.hu/index.php/hu/node/1521 <span class="field field--name-title field--type-string field--label-hidden">2019_Functional nanostructures</span> <div class="clearfix text-formatted field field--name-body field--type-text-with-summary field--label-hidden field__item"><h4><strong>2019</strong></h4> <p><strong>Metamagnetic transition in FeRh thin film.</strong> — It is known, that FeRh alloy undergoes first-order metamagnetic transition, from the low temperature antiferromagnetic (AFM) phase, to the high temperature ferromagnetic (FM) phase. In the AFM phase Fe atoms carry magnetic moment of ±3.3 μ<sub>b</sub> while Rh atoms possess inconsiderable magnetic moment. On the contrary, in the FM phase, Fe and Rh atoms carry parallel moments of 3.2 μ<sub>b</sub> and 0.9 μ<sub>b</sub> respectively. This magnetic transition is chaperoned by reduction of resistivity and by a ~0.6 % isotopic strain in the crystal lattice. By introducing strain in the FeRh crystal lattice, this phenomenon can be reversed and the magnetic transition can be triggered by deformation.</p> <p>Nuclear resonant scattering technique at different grazing angles was used to determine the depth resolution of magnetic configuration in the FeRh layer deposited on BaTiO<sub>3 </sub>(100) ferroelectric substrate in the temperature range between 25 °C and 165 °C. At room temperature, the FeRh layer exhibited mainly AFM ordering with the formation of FM layers on both upper and lower interface. At about 105 °C small FM regions appeared in the AFM layer, which showed ripening with further heating until the whole layer became FM at 165 °C.</p> <img alt="functional nanostructures1" data-entity-type="file" data-entity-uuid="9c5d6fc4-4c52-4541-a394-4f21484c892f" src="https://wigner.hu/sites/default/files/inline-images/functional%20nanostructures1.png" width="600" class="align-center" /> <p><em>Figure 1.  Model of temperature induced AFM/FM metamagnetic transition in FeRh thin film</em></p> <p><strong>Structuring of colloidal silica nanoparticle suspensions near water-silica interfaces.</strong> — Structuring of aqueous suspensions of colloidal silica nanoparticles near an isolated planar silica-water interface were studied by specular neutron reflectivity. We found clear evidence that suspensions of colloidal silica nanoparticles (with size of 163±7 Å) show a damped, oscillatory concentration profile normal to a planar silica-water interface. The wavelength of these oscillations decreases with increasing concentration, and typically exceeds the particle diameter by a factor of 2–3. The measured wavelengths obtained by neutron reflectivity agree very well with the one determined by direct force measurements with the AFM in the slit-geometry, which suggest that in both geometries the self-organization of the nanoparticles is governed by the same principles. The reflectivity further indicated that the oscillatory structure persists through few layers into the bulk and that its onset is separated from the interface by a particle free gap, whose width is about half the wavelength. The present study thus clearly demonstrates that the oscillatory concentration profile for an isolated surface has the same characteristics as for the slit-geometry. Such oscillatory profiles further reflect the liquid-like structuring in the bulk suspension. On the other hand, the particle-free gap seems to be specific to the nature of the surface. The present experimental results is a step forward to a better understanding of structuring of colloidal suspensions near interfaces.</p> <img alt="functional nanostructures 2" data-entity-type="file" data-entity-uuid="4384a6ee-803d-4ebf-b2c0-5a1de868c51d" src="https://wigner.hu/sites/default/files/inline-images/functional%20nanostructures2.png" width="300" class="align-center" /> <p><em>Figure 2. Oscillatory concentration profile of the silica nanoparticles in the normal direction to the interface.</em></p> <p> </p> </div> <span class="field field--name-uid field--type-entity-reference field--label-hidden"><span lang="" about="https://wigner.hu/index.php/hu/user/124" typeof="schema:Person" property="schema:name" datatype="" xml:lang="">Pentek Csilla</span></span> <span class="field field--name-created field--type-created field--label-hidden">cs, 07/02/2020 - 10:39</span> <div class="field field--name-field-ev field--type-datetime field--label-above"> <div class="field__label">Év</div> <div class="field__item"><time datetime="2019-01-02T12:00:00Z" class="datetime">sze, 01/02/2019 - 12:00</time> </div> </div> Thu, 02 Jul 2020 08:39:05 +0000 Pentek Csilla 1521 at https://wigner.hu 2018_Functional nanostructures https://wigner.hu/index.php/hu/node/916 <span class="field field--name-title field--type-string field--label-hidden">2018_Functional nanostructures</span> <div class="clearfix text-formatted field field--name-body field--type-text-with-summary field--label-hidden field__item"><h4><strong>2018</strong></h4> <p><strong>Iron Self-diffusion in Fe5Ge3 thin film</strong></p> <p>Iron-germanides are widely investigated due to their possible application in nanoelectronics and spintronics applications. The feasibility of these materials in industrial application is highly dependent on their structural stability against temperature, therefore it is indispensable to understand temperature induced diffusion processes in this system. [<sup>57</sup>Fe<sub>5</sub>Ge<sub>3</sub>(36 Å)/nFe<sub>5</sub>Ge<sub>3</sub>(62 Å)]10 isotope-periodic multilayer has been prepared by molecular beam epitaxy, in order to study iron self-diffusion in Fe<sub>5</sub>Ge<sub>3</sub>. By using neutron reflectivity technique, which is sensitive to atomic scale diffusion lengths, we have determined the pre-exponent factor and activation energy as D<sub>0</sub> = (8.22 ± 3.8) × 10<sup>-18 </sup>m<sup>2</sup>s<sup>−1</sup> and E<sub>a</sub> = (0.28 ± 0.02) eV respectively. <br /> <br /> <img alt="az3" data-entity-type="file" data-entity-uuid="221094a5-3a15-4e63-b274-80f7644f1d82" src="https://wigner.hu/sites/default/files/inline-images/az3.jpg" /><br /> <br /> <em><strong>Figure 1.</strong> Layer structure of Fe5Ge3 isotope periodic multilayer structure.</em></p> <p><strong>The effect of carboxylic acids on the core/shell structure of iron oxide nanoparticles</strong><br /> <br /> Core/shell nanoparticles have been in the center of scientific interest due to their possible applications in medicine and catalysis. The formation of magnetite/maghemite core/shell structure was studied by Mössbauer-, Raman- and infrared spectroscopies as well as by electronmicroscopy and x-ray diffractometry in coprecipitated iron oxide based nanocomposites functionalized with various carboxylic acids. The core/shell ratio of the nanomagnetites can be changed by the oxidation or the reduction of the particles. It was found that sometimes the phases cannot be determined with Mössbauer spectroscopy at room- or liquid nitrogen temperatures, but only if the samples are <br /> measured at the temperature of liquid helium. Our results have shown that alongside with the preparation atmosphere the time of the washing is also crucial parameter during the synthesis of nanomagnetites. We have also found that the previously found correlation between that carboxylic acids and core/shell ratio of the nanomagnetites, can be caused by the different acidity of the carboxylic acids used for the functionalization of the iron oxide nanoparticles. These novel finding can be helpful to adjust the core/shell ratio of the coprecipitated carboxylic acid coated nanomagnetites.  </p> <p><img alt="az1" data-entity-type="file" data-entity-uuid="684fd537-7f1c-4265-a6b1-8046c27e9730" src="https://wigner.hu/sites/default/files/inline-images/az1.jpg" /><br /> <br /> <em><strong>Figure 2.</strong> Schematic illustration of coating with carboxylic acids on nanomagnetite with the change of the thickness of meghemite shell.</em></p> <p> </p> <h4> </h4> </div> <span class="field field--name-uid field--type-entity-reference field--label-hidden"><span lang="" about="https://wigner.hu/index.php/hu/user/171" typeof="schema:Person" property="schema:name" datatype="" xml:lang="">Werovszky Veronika</span></span> <span class="field field--name-created field--type-created field--label-hidden">sze, 06/26/2019 - 10:51</span> <div class="field field--name-field-ev field--type-datetime field--label-above"> <div class="field__label">Év</div> <div class="field__item"><time datetime="2018-01-02T12:00:00Z" class="datetime">k, 01/02/2018 - 12:00</time> </div> </div> Wed, 26 Jun 2019 08:51:07 +0000 Werovszky Veronika 916 at https://wigner.hu 2017_Functional nanostructures https://wigner.hu/index.php/hu/node/1520 <span class="field field--name-title field--type-string field--label-hidden">2017_Functional nanostructures</span> <div class="clearfix text-formatted field field--name-body field--type-text-with-summary field--label-hidden field__item"><h4><strong>2017</strong></h4> <p><strong>In situ study of electric field controlled ion transport in the Fe/BaTiO</strong><strong>3</strong><strong> interface.</strong> — The development of more advanced devices which can reflect upon the challenges of our world requires the exploration of novel material properties. Special systems which combine magnetic and electronic properties into a multifunctional material are excellent subject of this demand. </p> <p>In multiferroic materials (in short <em>multiferroics</em>) the coexistence and coupling of ferroelectric and magnetic order enables the fine control and modulation of electric polarization by magnetic field (<em>direct magnetoelectric effect, ME</em>) or the magnetic field by electric polarization (<em>converse magnetoelectric effect</em>). The electric field control of magnetic spin will lead to significantly lower energy consumption in actuators, information storage and spintronics devices, a key issue for sustainable development. Not only the reduction of energy consumption but also the production of energy from ambient sources such as vibrations, sound, radiofrequency waves, light, temperature gradients and also novel medical applications give new perspectives for multiferroic materials.  The Fe/BTO system, as a great example of strong ME coupling, is an excellent system to investigate this phenomenon. Several works reported as well that an applied electric field can alter the properties of this system.</p> <p><img alt="f1" data-entity-type="file" data-entity-uuid="430a82fd-b12d-4c85-b8e0-8249f224bdb5" height="300" src="https://wigner.hu/sites/default/files/inline-images/K%C3%A9perny%C5%91fot%C3%B3%202018-11-27%20-%208.02.07.png" width="600" /></p> <p><strong><em>Figure 1.</em></strong><em> Nuclear forward scattering spectra as a function of deposited iron-57 on BaTiO</em><em>3</em><em> substrate in case of 0 V and 1 keV applied voltage.</em></p> <p>Electric field controlled ion transport and interface formation of iron thin films on a BaTiO3 substrate have been investigated by in situ nuclear resonance scattering and x-ray reflectometry techniques.  At early stage of deposition, an iron-II oxide interface layer was observed. The hyperfine parameters of the interface layer were found insensitive to the evaporated layer thickness. When an electric field was applied during growth, a 10 Å increase of the nonmagnetic / magnetic thickness threshold and an extended magnetic transition region was measured compared to the case where no field was applied. The interface layer was found stable under this threshold when further evaporation occurred, contrary to the magnetic layer where the magnitude and orientation of the hyperfine magnetic field vary continuously. The obtained results of the growth mechanism and of the electric field effect of the Fe/BTO system will allow the design of novel applications by creating custom oxide/metallic nanopatterns using laterally inhomogeneous electric fields during sample preparation (Fig.1). </p> <p><strong>Preparation of </strong><strong>57</strong><strong>Co (α-Fe) Mössbauer sources of uniform lateral activity distribution.</strong> — The quality of Mössbauer source can influence the experimental results, which may lead to false scientific conclusions. Due to the self-absorption of the resonant radiation by the daughter nuclei, the effective half-life of a radioactive Mössbauer source can be significantly decreased in case of high specific activity. For a given initial activity and source area, the lifetime is the longest for the homogenous lateral activity distribution. Besides, for the precise absolute determination of resonant line intensities, the time-dependent effective Lamb–Mössbauer factor of the source needs to be exactly known, a condition which can only be fulfilled for a laterally perfectly homogenous source. This is especially important in Mössbauer polarimetry, a unique laboratory method for the determination of the alignment and direction of magnetisation in buried layers of thin films and multilayers. Due to special geometric and radiation protection conditions, the necessary 57Co (α-Fe) sources are not available commercially.</p> <p><img alt="f2" data-entity-type="file" data-entity-uuid="a10ab4d9-3b36-4512-8602-596e9203d841" height="490" src="https://wigner.hu/sites/default/files/inline-images/K%C3%A9perny%C5%91fot%C3%B3%202018-11-27%20-%208.01.27.png" width="534" /></p> <p><strong><em>Figure 2.</em></strong><em> Activity distribution of </em><em>57</em><em>Co (α-Fe) sources prepared without (top) and with (bottom) using the new preparation technology, respectively.</em></p> <p>A new technology for preparing 57Co (α-Fe) Mössbauer sources of lateral activity homogeneity better than 10 % was elaborated and an application for its patenting has been filed. The homogeneity of the lateral activity distribution was verified by a newly developed scanning setup of about 250 μm lateral resolution. In Fig. 2, the lateral scans of the activity distribution of 57Co (α-Fe) sources prepared without (top) and with (bottom) using the new preparation technology are shown, respectively.  It can be seen, that a great improvement in the homogeneity could have been achieved, therefore this novel preparation technology of 57Co (α-Fe) source is expected to be used widely in Mössbauer polarimetry applications.</p></div> <span class="field field--name-uid field--type-entity-reference field--label-hidden"><span lang="" about="https://wigner.hu/index.php/hu/user/124" typeof="schema:Person" property="schema:name" datatype="" xml:lang="">Pentek Csilla</span></span> <span class="field field--name-created field--type-created field--label-hidden">h, 07/02/2018 - 10:36</span> <div class="field field--name-field-ev field--type-datetime field--label-above"> <div class="field__label">Év</div> <div class="field__item"><time datetime="2017-01-02T12:00:00Z" class="datetime">h, 01/02/2017 - 12:00</time> </div> </div> Mon, 02 Jul 2018 08:36:51 +0000 Pentek Csilla 1520 at https://wigner.hu