Current state of laser synthesis of metal and alloy nanoparticles as ligand-free reference materials for nano-toxicological assays

• Christoph Rehbock,
• Jurij Jakobi,
• Lisa Gamrad,
• Selina van der Meer,
• Daniela Tiedemann,
• Ulrike Taylor,
• Wilfried Kues,
• Detlef Rath and
• Stephan Barcikowski

Beilstein J. Nanotechnol. 2014, 5, 1523–1541, doi:10.3762/bjnano.5.165

• compositions are required, whose synthesis is reviewed in the next chapter. Laser-fabricated alloy nanoparticles with controlled composition In order to synthesize alloy nanoparticles with controlled elemental compositions AuAg proves to be an ideal model system as the phase diagram of gold and silver is

Designing magnetic superlattices that are composed of single domain nanomagnets

• Derek M. Forrester,
• Feodor V. Kusmartsev and
• Endre Kovács

Beilstein J. Nanotechnol. 2014, 5, 956–963, doi:10.3762/bjnano.5.109

• parameter a is shown through the phase diagram of Figure 1a for the two coupled nanomagnets systems that were also considered in [15]. In this phase diagram the AF1 phase occurs when [15] In this system the average magnetization, that evolves with the application of an external magnetic field, has a

• pertinent phase is shown. The phase diagrams in Figure 1a–c are found through the use of the quasi-static techniques described in [15]. The fourth phase diagram, Figure 1d, is found from the dynamical analysis by using the LLG equations (Equation 6). From Figure 1d one can see that the AP phase is the least

• solutions. In Figure 1b, the phase diagram for three coupled nanomagnets is shown. Again there are AF (1,2), AP, and P regimes. When the anisotropy is in the range there is an AF1 spin-flop phase. Whereas, when the system of three nanomagnets is designed with anisotropies in the range, the AF2 phase is

Oriented attachment explains cobalt ferrite nanoparticle growth in bioinspired syntheses

• Annalena Wolff,
• Walid Hetaba,
• Marco Wißbrock,
• Stefan Löffler,
• Nadine Mill,
• Katrin Eckstädt,
• Axel Dreyer,
• Inga Ennen,
• Norbert Sewald,
• Peter Schattschneider and
• Andreas Hütten

Beilstein J. Nanotechnol. 2014, 5, 210–218, doi:10.3762/bjnano.5.23

• evaluation. A tertiary phase diagram of the system CoFeO at room temperature needs to be determined before a useful evaluation of the phase transformations can be conducted. Further theoretical studies are therefore required to understand the underlying principles of these transformations. The fact that some

Plasticity of nanocrystalline alloys with chemical order: on the strength and ductility of nanocrystalline Ni–Fe

• Jonathan Schäfer and
• Karsten Albe

Beilstein J. Nanotechnol. 2013, 4, 542–553, doi:10.3762/bjnano.4.63

• embedded-atom (EAM) type potential which reproduces the phase diagram of Ni–Fe [20]. The hybrid method allows for structural relaxation by MD and for chemical equilibration by interleaving MC steps, yielding structurally equilibrated samples with an equilibrium distribution of the constituents. The MC

• , which show an ordered L12 structure inside the grains, lie outside the phase field of the L12 structure (at 600 K) in the bulk phase diagram reproduced by the interatomic potential [20]. The stability range of the ordered L12 structure in the phase diagram is therefore widened at reduced average grain

Focused electron beam induced deposition: A perspective

• Michael Huth,
• Fabrizio Porrati,
• Christian Schwalb,
• Marcel Winhold,
• Roland Sachser,
• Maja Dukic,
• Jonathan Adams and
• Georg Fantner

Beilstein J. Nanotechnol. 2012, 3, 597–619, doi:10.3762/bjnano.3.70

• structures by employing the precursors Me3Pt(IV)CpMe and neopentasilane (Si5H12), the latter one being used for the first time in FEBID experiments [28]. Metal-silicides are highly relevant for metallization layers in integrated circuits. More importantly, the binary Pt–Si phase diagram shows several

• intermetallic phases, two of which are superconductors. It is thus worthwhile discussing the Pt–Si system in some more detail. Pt–Si FEBID structures As already alluded to in the last subsection the binary phase diagram of the Pt–Si system reveals two intermetallic compounds, which have a superconducting ground

• to the next section. Co–Pt FEBID structures As a second example of a binary FEBID experiment recent results on the Co–Pt system are reviewed [33]. The binary phase diagram of Co–Pt features several ferromagnetic intermetallic compounds. The most prominent of these is the L10 phase of CoPt, which has

Size-dependent phase diagrams of metallic alloys: A Monte Carlo simulation study on order–disorder transitions in Pt–Rh nanoparticles

• Johan Pohl,
• Christian Stahl and
• Karsten Albe

Beilstein J. Nanotechnol. 2012, 3, 1–11, doi:10.3762/bjnano.3.1

• simulation; nanoparticles; nanothermodynamics; phase diagram; Pt-Rh; thermodynamics; Introduction Pt–Rh is an important alloy due to its catalytic activity in different reactions. In the past it was assumed that Pt–Rh is immiscible at low temperatures [1][2], but theoretical studies revealed that Pt–Rh

• forms the intermetallic phases 40 and D022 [3], which are thermodynamically stable below room temperature according to a recently published theoretical phase diagram [4] (see Figure 1 for the 40 and D022 structures). Boundaries in a bulk phase diagram are well defined in the case of the thermodynamic

• were studied by means of lattice Monte Carlo simulations [25]. However, as far as we know, a complete size-dependent phase diagram of an ordering nanoalloy has not yet been studied. It is our intention to examine such a size-dependent phase diagram by using the model system of Pt–Rh particles and

Surface induced self-organization of comb-like macromolecules

• Konstantin I. Popov,
• Vladimir V. Palyulin,
• Martin Möller,
• Alexei R. Khokhlov and
• Igor I. Potemkin

Beilstein J. Nanotechnol. 2011, 2, 569–584, doi:10.3762/bjnano.2.61

• respect to the B chains. In this case the whole phase diagram shifts towards lower values of β (one needs a smaller fraction of long side chains of B type to change the morphology). Partial desorption of the B side chains influences not only the morphology but also the size and aggregation number of the

• . Schematic representation of “holes” Phase diagram of the film in terms of the fraction of B side chains, β = NB/(NA + NB), and the spreading parameter SB. The line splits the regions of flat and prominent morphologies. The spreading parameter SA satisfies the inequality to ensure 2D conformation of A

Structural and magnetic properties of ternary Fe_1–xMn_xPt nanoalloys from first principles

• Markus E. Gruner and
• Peter Entel

Beilstein J. Nanotechnol. 2011, 2, 162–172, doi:10.3762/bjnano.2.20

• . The phase diagram of ternary Fe1–xMnxPt was examined experimentally in detail by Menshikov et al. [73] by means of X-ray and neutron diffraction measurements on a powder sample. The authors found that the alloy assumes a nearly, but not perfectly L10 ordered tetragonal structure for all compositions

Kinetic lattice Monte-Carlo simulations on the ordering kinetics of free and supported FePt L1₀-nanoparticles

• Michael Müller and
• Karsten Albe

Beilstein J. Nanotechnol. 2011, 2, 40–46, doi:10.3762/bjnano.2.5

• concentration of vacancies in the volume of the particle. In consequence, the absolute values of the interaction energies in the Ising-type Hamiltonian have to be adjusted in order to reproduce reasonable values for the vacancy formation energy. In doing so, important properties like the phase diagram and the

Preparation and characterization of supported magnetic nanoparticles prepared by reverse micelles

• Ulf Wiedwald,
• Luyang Han,
• Johannes Biskupek,
• Ute Kaiser and
• Paul Ziemann

Beilstein J. Nanotechnol. 2010, 1, 24–47, doi:10.3762/bjnano.1.5

• from the interior would shift the atomic composition of the core from Fe53Pt47 to Fe68Pt32. According to the FePt bulk phase diagram, such a compositional change would lead to a structural transformation into the Fe3Pt phase. In this case, the driving force of a decreasing total surface energy due to