Iron-dependent degradation of IRP2 requires its C-terminal region and IRP structural integrity-3

+) or without (-) tetracycline. (A and C) Cytoplasmic extracts were analyzed for IRE-binding activity with a P-labeled IRE probe in the absence or presence of 0.2 μg purified polyclonal HA antibody. The positions of the IRE/IRP complexes, the HA-supershifts and excess free IRE probe are indicated by arrows. (B) Analysis of TfR1 expression in two clones expressing IRP1-IRP2. Lysates were subjected to Western blotting with HA (top), TfR1 (middle) and β-actin (bottom) antibodies.<p><b>Copyright information:</b></p><p>Taken from "Iron-dependent degradation of IRP2 requires its C-terminal region and IRP structural integrity"</p><p>http://www.biomedcentral.com/1471-2199/9/15</p><p>BMC Molecular Biology 2008;9():15-15.</p><p>Published online 28 Jan 2008</p><p>PMCID:PMC2267205.</p><p></p

Iron-dependent degradation of IRP2 requires its C-terminal region and IRP structural integrity-4

Ks domains 3 and 4, and the C-terminal HA tag. (B-F) H1299 cells engineered to express the above mutants (in two or three independent clones) were treated overnight (14 h) with 30 μg/ml FAC and lysates were subjected to Western blotting with HA (top) and β-actin (bottom) antibodies. The different migration of wild type IRP2 and the ΔC60 and ΔC168 deletion mutants is illustrated in (B).<p><b>Copyright information:</b></p><p>Taken from "Iron-dependent degradation of IRP2 requires its C-terminal region and IRP structural integrity"</p><p>http://www.biomedcentral.com/1471-2199/9/15</p><p>BMC Molecular Biology 2008;9():15-15.</p><p>Published online 28 Jan 2008</p><p>PMCID:PMC2267205.</p><p></p

Iron-dependent degradation of IRP2 requires its C-terminal region and IRP structural integrity-1

RP2chimeras and the ΔD4 IRP1 deletion mutant; the IRP1 constructs are tagged with FLAG and the others with HA epitopes. (B-E) H1299 cells engineered to express wild type IRP1, ΔD4 IRP1, wild type IRP2 or the above chimeras (in three independent clones) were treated overnight (14 h) with 30 μg/ml FAC or 100 μM hemin, and lysates were subjected to Western blotting with FLAG or HA (top) and β-actin (bottom) antibodies.<p><b>Copyright information:</b></p><p>Taken from "Iron-dependent degradation of IRP2 requires its C-terminal region and IRP structural integrity"</p><p>http://www.biomedcentral.com/1471-2199/9/15</p><p>BMC Molecular Biology 2008;9():15-15.</p><p>Published online 28 Jan 2008</p><p>PMCID:PMC2267205.</p><p></p

Iron-dependent degradation of IRP2 requires its C-terminal region and IRP structural integrity-0

Ks domains 3 and 4, and the C-terminal HA tag. The 73 amino acids sequence (73d) within domain 1 is highlighted in gray. (B-G) H1299 cells engineered to express wild type IRP2 or two independent clones of the above mutants (except ΔD1) were treated overnight (14 h) with 100 μM hemin or 30 μg/ml FAC and lysates were subjected to Western blotting with HA (top) and β-actin (bottom) antibodies. No clones expressing ΔD1 could be isolated.<p><b>Copyright information:</b></p><p>Taken from "Iron-dependent degradation of IRP2 requires its C-terminal region and IRP structural integrity"</p><p>http://www.biomedcentral.com/1471-2199/9/15</p><p>BMC Molecular Biology 2008;9():15-15.</p><p>Published online 28 Jan 2008</p><p>PMCID:PMC2267205.</p><p></p

Iron-dependent degradation of IRP2 requires its C-terminal region and IRP structural integrity-2

E metabolically labeled for 2 h with S-methionine/cysteine. Subsequently, the cells were chased for the indicated time intervals in cold media in the absence or presence of 30 μg/ml FAC. Cytoplasmic lysates (500 μg) were subjected to quantitative immunoprecipitation with 1 μg HA (Santa Cruz) or FLAG (Sigma) antibodies. Immunoprecipitated proteins were analyzed by SDS-PAGE on a 7.5% gel and visualized by autoradiography. The radioactive bands were quantified by phosphorimaging. The percentage of residual radioactivity from three independent experiments (mean ± SD) is plotted against time.<p><b>Copyright information:</b></p><p>Taken from "Iron-dependent degradation of IRP2 requires its C-terminal region and IRP structural integrity"</p><p>http://www.biomedcentral.com/1471-2199/9/15</p><p>BMC Molecular Biology 2008;9():15-15.</p><p>Published online 28 Jan 2008</p><p>PMCID:PMC2267205.</p><p></p

Iron-dependent degradation of IRP2 requires its C-terminal region and IRP structural integrity-5

Ides of IRP2 (grey) at their C-termini. (B and C) H1299 cells engineered to express these constructs (in two independent clones) were treated overnight (14 h) with the indicated concentrations of FAC and lysates were subjected to Western blotting with luciferase (top) and β-actin (bottom) antibodies.<p><b>Copyright information:</b></p><p>Taken from "Iron-dependent degradation of IRP2 requires its C-terminal region and IRP structural integrity"</p><p>http://www.biomedcentral.com/1471-2199/9/15</p><p>BMC Molecular Biology 2008;9():15-15.</p><p>Published online 28 Jan 2008</p><p>PMCID:PMC2267205.</p><p></p

Ultrathin Nanosheets of Organic-Modified β‑Ni(OH)₂ with Excellent Thermal Stability: Fabrication and Its Reinforcement Application in Polymers

β-Nickel hydroxide (β-Ni­(OH)₂), which combines two-dimensional (2D) structure and the catalytic property of nickel-containing compounds, has shown great potential for the application in polymer nanocomposites. However, conventional β-Ni­(OH)₂ exhibits large thickness, poor thermal stability, and irreversible aggregation in polymer matrices, which limits its application. Here, we use a novel phosphorus-containing organosilane to modify the β-Ni­(OH)₂ nanosheet, obtaining a new β-Ni­(OH)₂ ultrathin nanosheet with excellent thermal stability. When compared to pristine β-Ni­(OH)₂, the organic-modified β-Ni­(OH)₂ (M-Ni­(OH)₂) maintains nanosheet-like structure, and also presents a small thickness of around 4.6 nm and an increased maximum degradation temperature by 41 °C. Owing to surface organic-modification, the interfacial property of M-Ni­(OH)₂ nanosheets is enhanced, which results in the exfoliation and good distribution of the nanosheets in a PMMA matrix. The addition of M-Ni­(OH)₂ significantly improves the mechanical performance, thermal stability, and flame retardancy of PMMA/M-Ni­(OH)₂ nanocomposites, including increased storage modulus by 38.6%, onset thermal degradation temperature by 42 °C, half thermal degradation temperature by 65 °C, and decreased peak heat release rate (PHRR) by 25.3%. Moreover, it is found that M-Ni­(OH)₂ alone can catalyze the formation of carbon nanotubes (CNTs) during the PMMA/M-Ni­(OH)₂ nanocomposite combustion, which is a very helpful factor for the flame retardancy enhancement and has not been reported before. This work not only provides a new 2D ultrathin nanomaterial with good thermal stability for polymer nanocomposites, but also will trigger more scientific interest in the development and application of new types of 2D ultrathin nanomaterials

Hexachloro-1,3-butadiene as a Functional Additive for Constructing an Efficient Solid Electrolyte Interface Layer for Long-Life Stable Li Anodes

Lithium (Li) metal is considered as one of the attractive anodes for next-generation high-energy-density batteries due to its ultrahigh theoretical specific capacity and low potential. However, many great challenges including uncontrolled dendrite growth and undesired side reactions during repeated cycling still seriously hinder its practical application in Li metal secondary batteries. Herein, we report the hexachloro-1,3-butadiene (HCBD) molecule as a functional additive to stabilize the Li anode by forming a stable solid electrolyte interface (SEI) layer with high Li ion conductivity via in situ surface and electrochemical reactions. Density functional theory calculations demonstrate that HCBD can preferentially react with the Li anode, which generates an ionic conducting species (LiCl) into an SEI layer. The LiCl-rich SEI layer effectively regulates Li+ deposition/stripping kinetics and then induces uniform nucleation of Li+ and reduces the side reactions between the Li anode and electrolyte. With an optimal amount of HCBD in an ether-based electrolyte, an excellent cycling lifespan (7000 h) was achieved with a low hysteresis voltage of ∼10 mV at 1.0 mA cm–2 in a Li||Li symmetrical cell. Furthermore, the LiFePO4-based cell with the additive-functionalized Li anode displays obviously improved cycling stability (with a high specific capacity of 141.1 mAh g–1 after 350 cycles at 1 C)

GMTs and seroprevalence of measles, mumps and rubella antibodies in different age group in 2011.

<p>GMTs and seroprevalence of measles, mumps and rubella antibodies in different age group in 2011.</p

Investigation of the Effect of Extra Lithium Addition and Postannealing on the Electrochemical Performance of High-Voltage Spinel LiNi_0.5Mn_1.5O₄ Cathode Material

The LiNi_0.5Mn_1.5O₄ (LNMO) spinel is an attractive cathode candidate for next generation lithium-ion batteries as it offers high power and energy density. In this paper, the effects of extra amounts of lithium addition and postannealing process on the physicochemical and electrochemical properties of the spherical LNMO material were investigated. The experimental results show that the amount of lithium and the postannealing process have significant impacts on the Mn³⁺ content, phase impurity (rock-salt phase) and phase structures (<i>Fd</i>3<i>m</i> and <i>P</i>4₃32) of the spherical LNMO cathode materials, so as their electrochemical performance. In particular, the phase transition from <i>Fd</i>3<i>m</i> to <i>P</i>4₃32 and the Mn³⁺ content of the LNMO spinels were found to be adjusted by lithium additions and the postannealing process. With the presence of Mn³⁺, the absence of the impurity phase (rock-salt phase) and the cation ordering in the spinels, the electrochemical rate performance and capacity retention of the products could be significantly improved. In a half cell test, LNMO cathode material with 5% of lithium excess (based on theoretical formula calculation) displays a high specific discharge capacity of 123 mAh g^–1 at 2 C rate with excellent capacity retention of 84% after 500 cycles at 55 °C. All these findings show the important roles of the synergic effects of Mn³⁺ content, phase impurity (rock-salt phase) and phase structures (<i>Fd3m</i> and <i>P</i>4₃32) on the electrochemical performance improvement of LNMO-based cathode materials, which will guide the preparation of LNMO-based cathode material with excellent electrochemical performance