Magneto-capacitance probing of the many-particle states in InAs dots
传感器的工作原理
传感器的工作原理Working Principles of Sensors。
Sensors are electronic devices that are designed to detect and respond to changes in the environment. They are widely used in various industries and applications, such as automotive, aerospace, medical, and consumer electronics. The working principles of sensors vary depending on their types and functions. In this article, we will discuss the most common working principles of sensors.1. Resistive Sensors。
Resistive sensors are based on the principle of changing resistance in response to changes in the environment. They consist of a sensing element and a signal conditioning circuit. The sensing element is made of a material that changes its resistance when exposed to a specific stimulus, such as temperature, pressure, or humidity. The signal conditioning circuit amplifies andconverts the resistance change into a measurable output signal, such as voltage or current.The most common types of resistive sensors are thermistors, strain gauges, and humidity sensors. Thermistors are used to measure temperature, strain gauges are used to measure strain and force, and humidity sensors are used to measure humidity.2. Capacitive Sensors。
磁学 径向克尔 英文 kerr effect
IntroductionThe Kerr effect, also known as the magneto-optic Kerr effect (MOKE), is a phenomenon that manifests the interaction between light and magnetic fields in a material. It is named after its discoverer, John Kerr, who observed this effect in 1877. The radial Kerr effect, specifically, refers to the variation in polarization state of light upon reflection from a magnetized surface, where the change occurs radially with respect to the magnetization direction. This unique aspect of the Kerr effect has significant implications in various scientific disciplines, including condensed matter physics, materials science, and optoelectronics. This paper presents a comprehensive, multifaceted analysis of the radial Kerr effect, delving into its underlying principles, experimental techniques, applications, and ongoing research directions.I. Theoretical Foundations of the Radial Kerr EffectA. Basic PrinciplesThe radial Kerr effect arises due to the anisotropic nature of the refractive index of a ferromagnetic or ferrimagnetic material when subjected to an external magnetic field. When linearly polarized light impinges on such a magnetized surface, the reflected beam experiences a change in its polarization state, which is characterized by a rotation of the plane of polarization and/or a change in ellipticity. This alteration is radially dependent on the orientation of the magnetization vector relative to the incident light's plane of incidence. The radial Kerr effect is fundamentally governed by the Faraday-Kerr law, which describes the relationship between the change in polarization angle (ΔθK) and the applied magnetic field (H):ΔθK = nHKVwhere n is the sample's refractive index, H is the magnetic field strength, K is the Kerr constant, and V is the Verdet constant, which depends on the wavelength of the incident light and the magnetic properties of the material.B. Microscopic MechanismsAt the microscopic level, the radial Kerr effect can be attributed to twoprimary mechanisms: the spin-orbit interaction and the exchange interaction. The spin-orbit interaction arises from the coupling between the electron's spin and its orbital motion in the presence of an electric field gradient, leading to a magnetic-field-dependent modification of the electron density distribution and, consequently, the refractive index. The exchange interaction, on the other hand, influences the Kerr effect through its role in determining the magnetic structure and the alignment of magnetic moments within the material.C. Material DependenceThe magnitude and sign of the radial Kerr effect are highly dependent on the magnetic and optical properties of the material under investigation. Ferromagnetic and ferrimagnetic materials generally exhibit larger Kerr rotations due to their strong net magnetization. Additionally, the effect is sensitive to factors such as crystal structure, chemical composition, and doping levels, making it a valuable tool for studying the magnetic and electronic structure of complex materials.II. Experimental Techniques for Measuring the Radial Kerr EffectA. MOKE SetupA typical MOKE setup consists of a light source, polarizers, a magnetized sample, and a detector. In the case of radial Kerr measurements, the sample is usually magnetized along a radial direction, and the incident light is either p-polarized (electric field parallel to the plane of incidence) or s-polarized (electric field perpendicular to the plane of incidence). By monitoring the change in the polarization state of the reflected light as a function of the applied magnetic field, the radial Kerr effect can be quantified.B. Advanced MOKE TechniquesSeveral advanced MOKE techniques have been developed to enhance the sensitivity and specificity of radial Kerr effect measurements. These include polar MOKE, longitudinal MOKE, and polarizing neutron reflectometry, each tailored to probe different aspects of the magnetic structure and dynamics. Moreover, time-resolved MOKE setups enable the study of ultrafast magneticphenomena, such as spin dynamics and all-optical switching, by employing pulsed laser sources and high-speed detection systems.III. Applications of the Radial Kerr EffectA. Magnetic Domain Imaging and CharacterizationThe radial Kerr effect plays a crucial role in visualizing and analyzing magnetic domains in ferromagnetic and ferrimagnetic materials. By raster-scanning a focused laser beam over the sample surface while monitoring the Kerr signal, high-resolution maps of domain patterns, domain wall structures, and magnetic domain evolution can be obtained. This information is vital for understanding the fundamental mechanisms governing magnetic behavior and optimizing the performance of magnetic devices.B. Magnetometry and SensingDue to its sensitivity to both the magnitude and direction of the magnetic field, the radial Kerr effect finds applications in magnetometry and sensing technologies. MOKE-based sensors offer high spatial resolution, non-destructive testing capabilities, and compatibility with various sample geometries, making them suitable for applications ranging from magnetic storage media characterization to biomedical imaging.C. Spintronics and MagnonicsThe radial Kerr effect is instrumental in investigating spintronic and magnonic phenomena, where the manipulation and control of spin degrees of freedom in solids are exploited for novel device concepts. For instance, it can be used to study spin-wave propagation, spin-transfer torque effects, and all-optical magnetic switching, which are key elements in the development of spintronic memory, logic devices, and magnonic circuits.IV. Current Research Directions and Future PerspectivesA. Advanced Materials and NanostructuresOngoing research in the field focuses on exploring the radial Kerr effect in novel magnetic materials, such as multiferroics, topological magnets, and magnetic thin films and nanostructures. These studies aim to uncover newmagnetooptical phenomena, understand the interplay between magnetic, electric, and structural order parameters, and develop materials with tailored Kerr responses for next-generation optoelectronic and spintronic applications.B. Ultrafast Magnetism and Spin DynamicsThe advent of femtosecond laser technology has enabled researchers to investigate the radial Kerr effect on ultrafast timescales, revealing fascinating insights into the fundamental processes governing magnetic relaxation, spin precession, and all-optical manipulation of magnetic order. Future work in this area promises to deepen our understanding of ultrafast magnetism and pave the way for the development of ultrafast magnetic switches and memories.C. Quantum Information ProcessingRecent studies have demonstrated the potential of the radial Kerr effect in quantum information processing applications. For example, the manipulation of single spins in solid-state systems using the radial Kerr effect could lead to the realization of scalable, robust quantum bits (qubits) and quantum communication protocols. Further exploration in this direction may open up new avenues for quantum computing and cryptography.ConclusionThe radial Kerr effect, a manifestation of the intricate interplay between light and magnetism, offers a powerful and versatile platform for probing the magnetic properties and dynamics of materials. Its profound impact on various scientific disciplines, coupled with ongoing advancements in experimental techniques and materials engineering, underscores the continued importance of this phenomenon in shaping our understanding of magnetism and driving technological innovations in optoelectronics, spintronics, and quantum information processing. As research in these fields progresses, the radial Kerr effect will undoubtedly continue to serve as a cornerstone for unraveling the mysteries of magnetic materials and harnessing their potential for transformative technologies.。
全超导磁体托卡马克装置 英语
全超导磁体托卡马克装置英语作文Title:Fully Superconducting Tokamak (FST)A Fully Superconducting Tokamak (FST) is a pioneering design in the realm of nuclear fusion research, aiming to harness the power of the stars for sustainable energy production. This essay will provide an overview of FST technology, its operational principles, and its significance in the quest for clean energy.The FST is based on the Tokamak configuration, a doughnut-shaped (toroidal) device that uses magnetic fields to confine plasma, the hot, ionized gas necessary for nuclear fusion reactions. Unlike traditional tokamaks that use copper coils for magnetic confinement, FSTs employ superconducting coils. These coils, operating at extremely low temperatures, can maintain strong magnetic fields with minimal electrical resistance, significantly enhancing the device's efficiency and operational time.The heart of an FST lies in its superconducting coils, which are cooled to cryogenic temperatures, typically near absolute zero, using liquid helium. At these temperatures, the coils become superconductors, meaning they can conductelectricity with zero resistance. This property allows for the creation of powerful, stable magnetic fields that can confine the plasma in the toroidal chamber for extended periods.The plasma, consisting of hydrogen isotopes such as deuterium and tritium, is heated to temperatures exceeding 100 million degrees Celsius, the conditions necessary for nuclear fusion to occur. The magnetic fields generated by the superconducting coils prevent the plasma from touching the chamber walls, which would cool the plasma and disrupt the fusion process.FST technology offers several advantages over conventional tokamaks. Firstly, the use of superconducting coils allows for a more compact design, reducing the overall size and cost of the device. Secondly, FSTs can operate continuously for extended periods, potentially leading to a steady-state fusion reactor that can provide a constant source of electricity. This is in contrast to traditional tokamaks, which can only operate in short bursts due to the limitations of their copper coils.The development of FSTs represents a significant step forward in the pursuit of clean, sustainable energy. Nuclear fusion, if successfully harnessed, could provide a virtuallylimitless supply of energy without the greenhouse gas emissions associated with fossil fuels or the radioactive waste produced by nuclear fission. FSTs, with their improved efficiency and operational stability, bring the dream of fusion power closer to reality.In conclusion, the Fully Superconducting Tokamak (FST) is a cutting-edge technology that promises to revolutionize the field of nuclear fusion. By employing superconducting coils to confine plasma, FSTs offer a more efficient and stable approach to fusion energy production. As research in this area continues, FSTs could pave the way for a future where clean, sustainable energy is a global reality.。
英语四级阅读理解科学家集资
英语四级阅读理解科学家集资Scientists say they have discovered hints of alienlife on th e Saturn’s moon. The discovery of a sort oflife was announc ed after researchers at the USspace agency,NASA,analyzed da ta from spacecraftCassini,which pointed to,the existence of m ethane-based form of life on Saturn’s biggest moon. Scientists have reportedly discovered cluesshowing primitive alien bein gs are"breathing" inTitan’s dense atmosphere filled with hy drogen.They argue that hydrogen gets absorbedbefore hittin g Titan’s planet-like surface coveredwith methane lakes and rivers. This,they s ay,points to the existence of some"bugs" consumingthe hydr ogen at the surface of the moon less than half the size of the Earth."We suggested hydrogen consumption because it’s the obvious gas for life to consumeon Titan,similar to the way we consume oxygen on Earth,"says NASA scientist Chris McKay."Ifthese signs do turn out to be a sign of life,it would be doubly exciting because it wouldrepresent a second form of life inde pendent from water-based life on Earth." To date,scientists have not yet detec ted this form of life anywhere,though there are liquid- water-based microorganisms on Earth that grow well on methane o r produce it as a wasteproduct. On Titan, where temperatures are around 90 Kelvin(minus 290 degrees Farenheit),amethan ebased organism would have to use a substance that is liquid as its medium forliving processes, but not water itself. Water is frozen solid on Titan’s surface and much too coldto supp ort life as we know it. Scientists had expected the Sun’s i nteractions with chemicals in the atmosphere toproduce a co ating of acetylene on Titan’s surface. But Cassini detected n o acetylene on thesurface. The absence of detectable ace tylene on the Titan’s surface can very well have a non-biological explanation,said Mark Allen,a principal investigator of the NASA Titan team."Scientific conservatism suggests that a biological explanation should be the last choiceafter all non-biological explanations are addressed,"Allen said."We have a lot of work to do torule out possible non-biological explanations. It is more likely that a chemical proce ss,withoutbiology,can explain these results."1、What have scientists found about Saturn?A.They have found a new moon orbiting Saturn.B.They have found methane-based life on Saturn.C.They have found methane-based life on Titan.D.They have found earthlike life on a Saturn’s moon.2、What do scientists say about Titan?A.There are life clues there.B.There is acetylene there.C.Water on Titan exists in the form of ice.D.Rivers and lakes there contain life formls.3、To date,scientists have not yet detected this form of life.(para graph 5)What does"thisform of life" refer to?A.Water-based life.B.Methane-based life.C.Liquid-water-based microorganisms.D.Gas-based life.4、What can be inferred from what Allen said?A.Scientists have different arguments over whether there is lif e on Titan.B.Scientists all agree that there is life on Titan.C.Scientists all suggest that a biological explanation is reason able.D.Scientists all agree that a non-biological chemical reaction is a possible explanation.5、Which of the following can replace the title of this passage?A.Earthlike Living Beings Found on Titan.B.Finding of One More Moon of Saturn.C.Titan,a New Satellite Found.D.A different Life Form, a Possibility.。
METHOD AND PLANT FOR SOLVENT-FREE MICROWAVE EXTRAC
专利名称:METHOD AND PLANT FOR SOLVENT-FREE MICROWAVE EXTRACTION OF NATURALPRODUCTS发明人:MENGAL, Philippe,MOMPON, Bernard申请号:EP94915607.0申请日:19940510公开号:EP0698076A1公开日:19960228专利内容由知识产权出版社提供摘要:the object of the invention, for the production of biological productsold\u00f3szermentesmikrohull\u00e1m\u00fa procedure, which consists of the following steps: material is placed in a closed space, abiol\u00f3giai old\u00f3szermentesen,thez\u00e1rtt\u00e9rben in biological material by microwave radiation and the biological material is treated in water with at least oner\u00e9sz\u00e9telp\u00e1rologtatj\u00e1k,as well as the cellstrukt\u00far\u00e1itfelrepesztik biological material, and the natural product, at least one r\u00e9sz\u00e9tfelszabad\u00edtj\u00e1k, the rest of the biological material akinyert separating natural productswhich procedure characteristic, thez\u00e1rtt\u00e9r (1) inside the megszak\u00edt\u00e1sokkalcs\u00f6kkentett microwaves during the application of pressure is applied.and with themikrohull\u00e1mokalkalmaz\u00e1s\u00e1val treated biological material, cellstrukt\u00far\u00e1ithat\u00e9konyabban repesztik apart,at least a part of the alkalmaz\u00e1s\u00e1nakid\u0151tartama under microwaves, heating the enclosed space (1), and that the resulting from the biological materialelp\u00e1rolg\u00e1s\u00e1b\u00f3l temperaturecs\u00f6kken\u00e9stkiegyenl\u00edtik,the application of microwaves, and the step of the inside of the enclosed space (1) lowering compression, the use ofas well as thez\u00e1rtt\u00e9r (1) heating in combination with each other, the natural product vizesdesztill\u00e1ci\u00f3val is produced in such a manner that the biologicalanyagb\u00f3lsz\u00e1rmaz\u00f3 together with steam is extracted.the object of the invention is tov\u00e1bb\u00e1berendez\u00e9s solvent free microwave extraction of biological products, which is composed of the following: - in a closed space (1),the enclosed space (1) which is arranged inside a microwave generator (2) is equippedwith\u00e9sh\u0151fokszab\u00e1lyozott (3) surrounded by a double wall, double wall ah\u0151fokszab\u00e1lyozott; (3), (4), the temperature ofszab\u00e1lyoz\u00f3f\u0171t\u0151eszk\u00f6zb\u0151l; the inside of the enclosed space (1) nyom\u00e1stcs\u00f6kkent\u0151 v\u00e1kuumszivatty\u00fab\u00f3l; (5), the enclosed space (1) kimenet\u00e9hezcsatlakoztatott kivezet\u0151eszk\u00f6zb\u0151l (6). a申请人:ARCHIMEX P.I.B.S.地址:Case Postale 31 F-56038 Vannes Cédex FR国籍:FR代理机构:Vidon, Patrice, et al更多信息请下载全文后查看。
名著中英文对照
The Voyage of the Beagle An Essay on the Principle ofPopulation The Interpretation ofDreams The History of the Decline and Fall of the Roman Empire
文学名著
The Iron Heel The People of the Abyss The Sea-Wolf The Son of the Wolf The White Fang Benito Cereno Billy Budd Moby Dick(The Whale) Typee Paradise Lost Paradise Regained A Dream of John Ball and A King's Lesson News from Nowhere Blix McTeague Moran of the Lady Letty The Octopus- A Story ofCalifornia Uncle Tom's Cabin Gulliver's Travels The Battle of the Books and Others Frankenstein Bride ofLammermoor Ivanhoe Rob Roy The Heat ofMid-Lothian The Antiquary The Talisman- A Tale of the Crusaders Waverley A Lover's Complaint A Midsummer Night's Dream All's Well That Ends Well As You Like It Cymbeline King John King Richard II King Richard III Love's Labour's Lost Measure for Measure Much Ado About Nothing Pericles, Prince of Type The Comedy of Errors King Henry the Fourth King Henry the Fifth King Henry the Sixth King Henry the Eighth The History of Troilus and Cressida The Life ofTimon of Athens
stochastic calculus for fractional brownian motion and related processes附录
kH (t, u)dWu = CH Γ (1 + α)
(2)
R
α (I− 1(0,t) )(x)dWx
(see Lemma 1.1.3). Therefore, the first equality is evident, since
0 R t
(kH (t, u))2 x)α )2 dx +
k n
2H
2
.
C . n2
(B.0.12)
References
[AOPU00] Aase, K., Øksendal, B., Privault, N., Ubøe, J.: White noise generalization of the Clark-Haussmann-Ocone theorem with applications to mathematical finance. Finance Stoch., 4, 465–496 (2000) [AS96] Abry, P., Sellan, F.: The wavelet-based synthesis for fractional Brownian motion proposed by F. Sellan and Y. Meyer: Remarks and fast implementation. Appl. Comp. Harmon. Analysis, 3, 377–383 (1996) [AS95] Adler, R.J.; Samorodnitsky, G.: Super fractional Brownian motion, fractional super Brownian motion and related self-similar (super) processes. Ann. Prob., 23, 743–766 (1995) [ALN01] Al` os, E., Le´ on, I.A., Nualart, D.: Stratonovich stochastic calculus with respect to fractional Brownian motion with Hurst parameter less than 1/2. Taiwanesse J. Math., 5, 609–632 (2001) [AMN00] Al` os, E., Mazet, O., Nualart, D.: Stochastic calculus with respect to fractional Brownian motion with Hurst parameter less than 1/2. Stoch. Proc. Appl., 86, 121–139 (2000) [AMN01] Al` os, E., Mazet, O., Nualart, D.: Stochastic calculus with respect to Gaussian processes. Ann. Prob., 29, 766–801 (2001) [AN02] Al` os, E., Nualart, D.: Stochastic integration with respect to the fractional Brownian motion. Stoch. Stoch. Rep., 75, 129–152 (2002) [And05] Androshchuk, T.: The approximation of stochastic integral w.r.t. fBm by the integrals w.r.t. absolutely continuous processes. Prob. Theory Math. Stat., 73, 11–20 (2005) [AM06] Androshchuk, T., Mishura Y.: Mixed Brownian–fractional Brownian model: absence of arbitrage and related topics. Stochastics: Intern. J. Prob. Stoch. Proc., 78, 281–300 (2006) [AG03] Anh, V., Grecksch, W.: A fractional stochastic evolution equation driven by fractional Brownian motion. Monte Carlo Methods Appl. 9, 189–199 (2003)
Unit 5.Force of nature. ppt
Louis Pasteur Some of his works are: separation of mirror image molecules and effect of polarized light identification of the parasite that was killing silkworms James Maxwell He is known for the "Treatise on Electricity and Magnetism" published in 1873. Maxwell independently developed the "Maxwell-Boltzmann kinetic theory of gases". Edwin Hubble "Hubble's Law" stated that galaxies move away from each other at a speed determined by the distance that separated them. He classified galaxies as per their distance, shape, brightness patterns and content. Paul Dirac He received a Nobel prize in 1933 for the work on antiparticles. The "Dirac equation" was a version of the Schrodinger's equation.
Barbara Goldsmith is a noted author, historian. Her best-selling books include The Straw Man, Little Gloria…Happy at Last, Johnson v. Johnson, and Other Powers: The Age of Suffrage, Spiritualism, and the Scandalous Victoria Woodhull (soon to be a major motion picture produced by Kathleen Kennedy for Universal Studios) and Obsessive Genius: The Inner World of Marie Curie. Barbara Goldsmith has long been at the forefront of the effort to preserve our written heritage. She is the donor of the Goldsmith Conservation and Preservation Laboratories at the New Yse Divisions were recently named in her honor.
(2008)Dimensionality reduction: A comparative review
L.J.P. van der Maaten ∗ , E.O. Postma, H.J. van den Herik
MICC, Maastricht University, P.O. Box 616, 6200 MD Maastricht, The Netherlands.
22 February 2008
the number of techniques and tasks that are addressed). Motivated by the lack of a systematic comparison of dimensionality reduction techniques, this paper presents a comparative study of the most important linear dimensionality reduction technique (PCA), and twelve frontranked nonlinear dimensionality reduction techniques. The aims of the paper are (1) to investigate to what extent novel nonlinear dimensionality reduction techniques outperform the traditional PCA on real-world datasets and (2) to identify the inherent weaknesses of the twelve nonlinear dimenisonality reduction techniques. The investigation is performed by both a theoretical and an empirical evaluation of the dimensionality reduction techniques. The identification is performed by a careful analysis of the empirical results on specifically designed artificial datasets and on the real-world datasets. Next to PCA, the paper investigates the following twelve nonlinear techniques: (1) multidimensional scaling, (2) Isomap, (3) Maximum Variance Unfolding, (4) Kernel PCA, (5) diffusion maps, (6) multilayer autoencoders, (7) Locally Linear Embedding, (8) Laplacian Eigenmaps, (9) Hessian LLE, (10) Local Tangent Space Analysis, (11) Locally Linear Coordination, and (12) manifold charting. Although our comparative review includes the most important nonlinear techniques for dimensionality reduction, it is not exhaustive. In the appendix, we list other important (nonlinear) dimensionality reduction techniques that are not included in our comparative review. There, we briefly explain why these techniques are not included. The outline of the remainder of this paper is as follows. In Section 2, we give a formal definition of dimensionality reduction. Section 3 briefly discusses the most important linear technique for dimensionality reduction (PCA). Subsequently, Section 4 describes and discusses the selected twelve nonlinear techniques for dimensionality reduction. Section 5 lists all techniques by theoretical characteristics. Then, in Section 6, we present an empirical comparison of twelve techniques for dimensionality reduction on five artificial datasets and five natural datasets. Section 7 discusses the results of the experiments; moreover, it identifies weaknesses and points of improvement of the selected nonlinear techniques. Section 8 provides our conclusions. Our main conclusion is that the focus of the research community should shift towards nonlocal techniques for dimensionality reduction with objective functions that can be optimized well in practice (such as PCA, Kernel PCA, and autoencoders).
Complex magnetic interactions and charge transfer effects in highlyorderedNixFe1-x nano-wires
Complex magnetic interactions and charge transfer effectsin highly ordered Ni x Fe1Àx nano-wiresShu-Jui Chang,Chao-Yao Yang,Hao-Chung Ma,Yuan-Chieh Tseng nDepartment of Materials Science&Engineering,National Chiao Tung University,1001Ta Hsueh Road,Hsin-Chu30010,Taiwan,ROCa r t i c l e i n f oArticle history:Received23October2012Received in revised form12November2012Available online3December2012Keywords:NiFeNano-wiresXMCDCharge transfera b s t r a c tThis work investigates the subtle magnetic interactions within the Ni x Fe1Àx(x¼0.3,0.5,and1.0)nano-wires by probing spin-dependent behaviors of the two constituted elements.The wires were fabricatedby electro-deposition and an anode aluminum oxide template to produce free-standing nature,and theNi–Fe interactions were probed by x-ray magnetic spectroscopy across a BCC-FCC structuraltransition.The wires’magneto-structural properties were predominated by Ni,as reflected by adecrease but an increase in total magnetization and FCC x-ray intensity with increasing x,even if the Femoment increased simultaneously.Upon annealing,a prominent charge transfer,together with thechanges of spin-dependent states,took place in the Ni and Fe3d orbitals,and a structural disorderingwas also obtained,for the wires at x¼0.3.The charge transfer led to a local magnetic-compensation forthe two elements,explaining the minor change in total magnetization for x¼0.3probed by avibrational sample magnetometer.When x was increased to0.5,however,the charge transfer becameinactive due to persistent structural stability supported by Ni,albeit resulting in nearly invariantmagnetization similar to that of x¼0.3.The complexity of the Ni–Fe interactions varied with thecomposition and involved the modifications of the coupled magnetic,electronic and structural degreesof freedom.The study identifies the roles of Ni and Fe as unequally-influential in Ni x Fe1Àx,whichprovides opportunities to re-investigate the compound’s properties concerning its technologicalapplications.&2012Elsevier B.V.All rights reserved.1.IntroductionBecause permalloy(Ni80Fe20)[1,2]and invar(Ni65Fe35)[3,4]alloys are the central components of many modern technologies,shaping Ni x Fe1Àx into various forms in a controllable manner,andinvestigating the varying properties corresponding to the shapinghave captured great research popularity.Although the propertiesof Ni x Fe1Àx have been reported in several systems[5,6],probingNi–Fe interactions in nanostructures continues to provide aplayground for realizing the compound’s fundamental properties,as well as for developing principles to create the functionalstructures.Motivated by this cause,we combined pulse-electrodepositionand an anodic aluminum oxide(AAO)template to fabricateNi x Fe1Àx nano-wires with a precise control over the size andshape.The wires’coupled magnetic,electronic and structuraldegrees of freedom that determine the wires’macroscopic mag-netism were realized by the element-specific probes of Ni and Fe.An annealing-induced,spin-dependent Ni–Fe charge transfereffect was especially focused in this study.The modifications inmicroscopic magnetism,and associated electronic re-establish-ments,are often neglected if changes in macroscopic magnetismare imperceptible.Nevertheless,the invisible electronic interac-tions are essential,as they drive the magnetic ordering,alsoserving as the cause for many anomalous effects.This is a seriousconcern in Ni x Fe1Àx,because the compound disobeyed the Slater–Pauling prediction[7,8]at certain compositions,depending on thesystem and treatment[9,10].This implies that the magnetism ofNi x Fe1Àx is not simply the sum of the local moments of Ni and Febut rather depends on the local interactions of the two.Theinteractions may vary with x,because increasing x altered thecrystallographic structure of Ni x Fe1Àx[5,6].The underlying phy-sics is still under debate due to incomplete understanding ofNi x Fe1Àx and hence is worthy of exploration.Using x-ray magnetic spectroscopy,we successfully discrimi-nated the magnetisms of Ni and Fe with varying x.Further,employing rapid thermal annealing(RTA)we were able to createstructural instability,and examine the correlation between thestructural instability and the wires’magnetic and electronicresponses with x-dependency,based on the isolated Ni(Fe)behaviors.We discovered aflow of spins from Fe to Ni3dconduction band when the structural stability was lost,despiteContents lists available at SciVerse ScienceDirectjournal homepage:/locate/jmmmJournal of Magnetism and Magnetic Materials0304-8853/$-see front matter&2012Elsevier B.V.All rights reserved./10.1016/j.jmmm.2012.11.037*Corresponding author.Tel.:þ88635731898;fax:þ88635724727.E-mail address:yctseng21@.tw(Y.-C.Tseng).Journal of Magnetism and Magnetic Materials332(2013)21–27the total magnetization of the wires remaining almost unaltered. This resulted in a decrease but an increase in Fe and Ni local moments,together with the changes of the electronic states of the two.The element-specific probe uncovered the local magnetic-compensation of the wires invisible to the conventional probes, perfectly explaining the minor change in magnetization upon annealing.However,such phenomenon was absent when the structural stability was persistent,which can be related to the increased dominance of Ni.In summary this work investigates the properties of the Ni x Fe1Àx bimetallic wires from a microscopic picture.This work subverts our thoughts that the two elements are equally-influential in Ni x Fe1Àx,and therefore opens research opportunities concerning the compound’s properties from both technical and fundamental aspects.2.ExperimentalPulse-electrodeposition method combined with an AAO tem-plate were used to fabricate highly aligned Ni x Fe1Àx nano-wires with varying compositions(x¼0.3,0.5,and1).To do so,a commercial AAO featuring60m m in thickness and0.25m m in pore-diameter(aspect-ratio¼300)was patterned by a Ti/Cu electrode only on one side using a sputtering facility,where Ti served as an adhesion layer between the AAO and the Cu seed layer.The AAO inter-pore distance was about0.45m m.The Cu seed layer of the Ti/Cu electrode was not completely homoge-neous,so an extra Cu-electrodeposition on the AAO/Ti/Cu was followed to provide better quality of Cu,operating at a deposition current of15mA and a deposition time of1.5h.Afterwards,the AAO/Ti/Cu was immersed into a deposition bath containing FeSO4Á7H2O,NiSO4Á6H2O,H3BO3and ascorbic acid,subjected to an electrodeposition operated at30mA and a total duration of 20min.The deposition was pulse-based,with an interval of1s between current-on and-off,at which on and off were both held for1s in an alternating manner for the entire deposition.Since the pulse-delay time(T off)was kept constant,the anomalous co-deposition of Ni and Fe that may result in a higher deposition rate of Fe,as suggested by Salem et al.[11],was not expected in our case.The concentrations of Ni and Fe were controlled by the use of FeSO4Á7H2O and NiSO4Á6H2O,and were identified by energy dispersive spectrometry(EDX),subsequent to the removal of the wires from the substrate.The EDX analysis only showed Ni and Fe signals,which excluded the possibility that Cu electrode may form the alloy with NiFe upon annealing.RTA of3001C-2min was applied to the samples,and the annealed samples were compared with the non-annealed ones in terms of all analyses.The samples’morphologies,crystallographic structures and magnetic proper-ties were identified using a scanning electron microscope(SEM), an x-ray diffraction(XRD)facility and a vibrating sample magneto-meter(VSM),respectively,all without the AAO protec-tion.The wires’magnetic easy-axis was found to be the long-axis, so the magnetic hysteresis(M–H)curves presented here were all taken from the long-axis measurements.A high-resolution trans-mission electron microscope(HRTEM,JEM-2100F,operated at 200keV)was used to probe the microstructure of the wires.To further understand the wires’magnetism with elemental specifi-city,x-ray absorption spectroscopy(XAS)and x-ray magnetic circular dichrosim(XMCD)taken with total electron yield(TEY) and totalfluorescence yield(TFY)modes were employed to probe the spin-dependent states of Ni and Fe,at BL11A,National Synchrotron Radiation Research Center(NSRRC).The XMCD spectra were taken by having the x-ray photon wave-vector parallel to the wires’long-axis under an appliedfield of1T.This forced the Ni and Fe moments to be measured in a way parallel to the wires’easy-axis,which promised a quantitative comparison with the VSM data.Each XAS/XMCD spectrum presented in this work was the average of more than5data points collected on different spots of the same sample,and the deviation was very minor among the spectra,which suggests the sample homogene-ity to be of reliable quality.Finally,spin(S z)and orbital(L z) moments were estimated by sum-rule analysis[12]to elucidate the Ni and Fe moments in a detailed way.The use of n3d in sum-rule analysis was carefully treated,as detailed in the text, considering the varying electronic states of Ni and Fe.3.Results and discussionFig.1(a)shows the SEM image of the Ni x Fe1Àx nano-wires on the Ti/Cu electrode after the AAO removal,where the high-ordering,free-standing nature of the wires can be clearly assessed.The wires’dimensions were precisely controlled by the AAO and they were identical for all compositions in order to have a quantitative comparison in magnetic properties.Upon the RTA,the morphologies of the wires remain unaltered as con-firmed by Fig.1(b).The isolations of the wires were well preserved as demonstrated by SEM with a larger magnification.Wefirst focus on the wires without the RTA treatment. Fig.2(a)shows the x-dependent M–H curves for the wires.The saturationfield and coercivefield of the wires highly depend on the manufacturing recipe[13–15],aspect-ratio[16]and pore-diameter[11,14,17,18].In our case,the saturationfield is larger than5000Oe and the coercivefield is about75Oe inaverage.Fig.1.(a)Cross-sectional SEM image of the as-deposited Ni x Fe1Àx nano-wires and (b)top-viewed SEM image of the annealed Ni x Fe1Àx nano-wires,with a larger magnification.S.-J.Chang et al./Journal of Magnetism and Magnetic Materials332(2013)21–27 22The wires appear to lose saturation magnetization (M s )with increasing x .This suggests that the role of Ni is to reduce the wire’s magnetization,agreeing well with the general picture of the Slater–Pauling curve [9,10].Element-specific M –H curves performed over the L 3-edges of Ni and Fe are given in Fig.2(b).The Ni and Fe share similar field-dependency as shown in the M –H curves probed by the VSM (Fig.2(a)),suggesting that the two elements are coherent in magnetization reversal.A HRTEM image demonstrating a homogeneous polycrystalline microstructure for x ¼0.5is shown in Fig.2(c).Similar micrograph is seen in other samples (hence,not provided),in agreement with the literatures [9,18]reporting that the electro-deposition generally produces a polycrystalline microstructure for nano-materials.Upon the introduction of Ni,a structural transition takes place,changing from mainly BCC (x ¼0.3)[19],then BCC þFCC (x ¼0.5)[5,17,20]and finally to FCC (x ¼1.0)[21],as shown in Fig.2(d).The structural transition can be tracked by the transition of the characteristic peaks;i.e.,the Fe BCC-(110)setting at 45.23degree (x ¼0.3),then shifting to a lower angle of 44.15degree corre-sponding to the BCC–FCC mixed case (x ¼0.5),and finally relocat-ing at a higher angle of 44.76degree assigned by Ni FCC-(111)(x ¼1.0).The transition of the characteristic peaks is consistent with Glaubitz et al.[5]also dealing with a BCC -FCC transition in the Ni x Fe 1Àx thin films.It came to our attention that the structural ordering of the Fe-rich sample is weaker than that of the Ni-rich sample,from the fact that the Fe-rich sample’s (x ¼0.3)XRD intensity is less pronounced than that of the Ni (x ¼1.0)one.One may notice that the intensity of Cu (111)increases with increasing x ,therefore arguing that the crystallization of Ni could have been facilitated by a better crystallized Cu electrode,rather than an intrinsic property of Ni itself.However,all the AAO/Ti/Cu substrates were prepared in the same batch and the quality-variation was very minor.This can be validated by the comparable peak intensities of Cu (200)and Cu (220)from sample to sample.Therefore,the enhanced intensity of Cu (111)could be explained as having an overlap with the Ni (111)but not the quality-variation of the electrode.Thus,the results imply that the Ni FCC is more energetically favored within the wire struc-ture.This could explain the dominance of Ni over the wire’s magnetic properties as detailed below,considering that the structural and magnetic properties are often coupled in magnetic materials [22–25].The Ni and Fe XAS spectra with varying x are presented in Fig.3(a)and (b),respectively.Both Ni and Fe are found to be oxidized by the evidence of edge-splitting.In general,Fe is more sensitive to oxidation than Ni due to a higher oxidation potential [26],and the oxidation that can be easily acquired at the L 3as this edge,especially with the TEY XAS,is renowned for fingerprinting the chemical state of Fe [27–30].In XAS,x -dependency is almost imperceptible for Ni and Fe.However,XMCD reflecting the Ni and Fe moments exhibits opposite dependencies with x .In Fig.4(a),the Ni XMCD intensity is found to decrease with increasing x .Conversely,the Fe XMCD intensity not only increases but also turns to be more metallic-like with increasing x ,as presented in Fig.4(b).For x ¼0.5in particular,its Fe XMCD line-shape deviates from those of Fe 2O 3and Fe 3O 4[27,28]but is rather similar to metallic Fe [5,12],which suggests that the oxidation is minor for this concentration.Also,from the TEM results (not shown)we did not obtain any oxidized layer at the wire’s surface.For Fe,the XAS with light oxidation but the XMCD with a metallic spectral shape can be found in Tsai et al.[29]and Kim et al.[30],for the cases of CoFeB/MgO thin films and Fe substrate,respectively,very similar to our situation.In both references Fe was treated to be metallic and ferromagnetic considering the limited oxidation effect,and therefore the same principle can be followed for x ¼0.5here.However,the Fe oxidation cannot be neglected in x ¼0.3,as the oxidation effect is evident in the XMCD spectralshape.Fig.2.(a)x -Dependent M –H curves.(b)TFY M –H curves of Fe (black)and Ni (red)for x ¼0.5,and the same curve is seen in x ¼0.3.(c)HRTEM image of x ¼0.5.Similar polycrystalline microstructure is seen in x ¼1.0and 0.3.(d)x -dependent XRD patterns.For the FCC–BCC mixed phase case as x ¼0.5,the characteristic peaks are hard to identify so they are not indexed.However,for x ¼0.3,the characteristic peaks are close to Fe BCC so they are indexed.(For interpretation of the references to color in this figure legend,the reader is referred to the web version of this article.)S.-J.Chang et al./Journal of Magnetism and Magnetic Materials 332(2013)21–2723Fig.4(c)presents the x -dependent sum-rule analyses (S z þL z )for Ni and Fe.Qualitatively,the microscopic analyses from the sum rule are consistent with the macroscopic analyses from the VSM throughout the paper,indicating the reliability of the analyses.The sum-rule results suggest that Ni and Fe exhibit contrary dependencies,where the Fe moment increases,whereas the Ni moment decreases,with increasing x .The increased Fe moment can be explained by the more metallic and enhanced Fe XMCD as x increases from 0.3to 0.5(Fig.4(b)),while the decreased Ni moment can be understood as the suppressed XMCD signal,with increasing x ,after spectral normalization [31].The weighted sum of Ni and Fe presumably equals to the total magnetization of Ni x Fe 1Àx ,which decays with increasing x .It is noteworthy that the same trend has been discovered in Fig.8of Glaubitz et al.[5].Both Glaubitz’s and our results show the fact that despite Ni x Fe 1Àx following the Slater–Pauling prediction for magnetism,Ni and Fe take contrary paths locally,in spite of their coherent magnetization reversal.Interestingly,despite unclear mechanism for the decreased Ni moment with increasing x ,when concentration is weighted Ni’s magnetic strength is still sufficient to pull down the wire’s total magnetization matching the Slater–Pauling prediction.In combination with the XRD (Fig.2(c)),Ni seems to be more dominant than Fe in terms of magnetic and structural degrees of freedom,as will be further validated by the results from the RTA in the following.Now we turn focus to the RTA effects particularly for x ¼0.3and 0.5samples.Fig.5(a)and (b)presents the M –H curves and XRD patterns for x ¼0.3affected by the RTA,respectively.The saturation magnetization drops by only 5%with the RTA,so the magnetism is affected by the treatment in a very minor way.However,for x ¼0.3,notable changes are obtained in the Ni/Fe XAS (Fig.5(c)and (d)),with the Ni and Fe XAS white-line intensities being suppressed and enhanced,respectively.The XAS here corresponds to the Ni/Fe 2p -3d photo-excitation process with the white-line intensity reflecting the available vacancy in the 3d orbital.Since Ni exhibits suppressed intensity than that of Fe,it indicates a charge transfer from Fe to Ni via orbital hybridization that results in higher d-band vacancy of Fe,i.e.,a more oxidized state for Fe but a more reduced state for Ni,under the influence of the RTA.The more oxidized state for Fe is due to a more pronounced intensity in L 3pre-edge,while a more reduced state for Ni is linked to the suppressed XAS along with the disappearance of the shoulders around the edges.The charge transfer consequently modifies the spin-polarizations of the two constituents as reflected by their XMCD,as given in Fig.5(e)and (f).For Ni,the suppressed XAS gives rise to an enhanced XMCD as a consequence.Conversely,oscillation emerges in the Fe XMCD around the L 3,indicating a highly oxidized Fe as Fe 2O 3and Fe 3O 4[27,28].In Fig.5(b),the Fe BCC is found to disappear after the RTA.In fact,a heavily smeared peak near Cu (111)is barely detectable in the XRD of the annealed x ¼0.3,which can be due to the disappeared Fe (110).This indicates that some degrees of structural ordering still persist upon RTA to support the magnetic hysteresis observed in Fig.5(a),but it is difficult to be identified due to limited resolution of the x-ray facility,so we rather prefer to claim the phase to be close to amorphous.This is unusual because the heat treatment usually facilitates the crystallization of the materials especially in bulk forms.However,since the Ni x Fe 1Àx is formed in nano-wires,the large thermal stress raised by the RTA in a very short period is unlikely to be relieved within such a low and confined dimension,and therefore causes deterioration of the structure,especially when the structural ordering is intrinsically weak prior to the RTA.Here,the Ni–Fe charge transfer occurs with the disappear-ance of Fe (110),perhaps due to more overlapped Ni/Fe 3d electron wave-functions with the structural disordering,and examples of structural-disordering induced charge transfer can be referred to from Refs.[32–34].Since the magnetic and structural properties are strongly coupled,the annealing-induced structural disordering would modify the magnetism of Ni x Fe 1Àx accordingly.Interestingly,though the modification is obscure with a macroscopic probe,it is unambiguously probed by a microscopic one,hence revealing the importance of the latter.Fig.6presents the sum-rule results (S z þL z )for Ni and Fe before and after the RTA,for x ¼0.3.Considering the substantial changes in the chemical states of Ni and Fe,n 3d for both metallic and fully oxidized (Ni 2þ,Fe 3þ)cases were used in various combinations to examine if any deviation in the trend of (S z þL z )is seen.The deviation was less than 15%for the extreme case and had no significant influence on the trend.The results reveal that the charge transfer is spin-dependent,resulting in a decrease but an increase in the Fe and Ni moments.Therefore,the minor magnetization change probed by the VSM (Fig.5(a))can be understood as a local magnetic-compensation.It arises from the spin exchange between the two elements with the loss of structural stability,a phenomenon invisible to the conventional measurement.For x ¼0.5,the magnetization also drops imperceptibly after the RTA,as shown in Fig.7(a).However,the induced structural disordering is less pronounced than that of x ¼0.3,as the char-acteristic peaks of the mixed-phase are still visible in Fig.7(b),especially the peak near Cu(111).The persistence of structural stability deactivates the electronic modifications of Ni and Fe,as reflected by their XAS provided in Fig.7(c)and (d),respectively.Fig.3.x -Dependent (a)Ni L 2,L 3XAS and (b)Fe L 2,L 3XAS.S.-J.Chang et al./Journal of Magnetism and Magnetic Materials 332(2013)21–2724Fig.4.x -Dependent (a)Ni L 2,L 3XMCD and (b)Fe L 2,L 3XMCD.All spectra are normalized to the integrations of corresponding XAS spectra.(c)Sum-rule (S z þL z )analyses for Ni,Fe,and weighted Ni þFe,with x -dependency.In (c),lines through data points are guides for the eyes,and the scale of the y -axis is selectively presented for the purpose ofclarity.Fig.5.(a)M –H curves (b)XRD patterns (c)Ni L 2,L 3XAS (d)Fe L 2,L 3XAS (e)Ni L 2,L 3XMCD and (f)Fe L 2,L 3XMCD,for x ¼0.3before and after the RTA treatment.S.-J.Chang et al./Journal of Magnetism and Magnetic Materials 332(2013)21–2725Here,the Ni XAS remains unaltered,but a minor deviation is obtained in the Fe XAS after the RTA,and a likeness is seen in their XMCD (Fig.7(e)and (f)).The identical Ni XAS before and after the RTA suggests no electronic-modification;i.e.,no charge transfer in the Ni conduction band.Thus,the limited change in the Fe XAS can be realized as the minor oxidation at the surface,instead of the electron removal as that happened at x ¼0.3.Apparently,thecharge transfer effect is both composition-and structure-dependent.It only occurs when the structural stability is lost such as x ¼0.3.However,for x ¼0.5,the charge transfer is invisible,due to the robust structural stability supported by the larger fraction of the Ni FCC.The results indicate that the properties of Ni x Fe 1Àx are complex,involving the interactions among the magnetic,structural and electronic degrees of freedom which all vary with x ,and are probably hard to be predicted by the Slater–Pauling curve alone.In particular,the role of Ni is found to be supreme in Ni x Fe 1Àx as it dominates the total magnetization and structural stability,and thus its influence should be more weighted than Fe,which is essential for attempts to tailor the properties of Ni x Fe 1Àx .In bimetallic magnetic compounds,we find that if one of the constituents dominates the magnetic properties,there must be at least a physical parameter,such as crystal or electronic structure itinerantly coupled with the magnetism of the dominant consti-tuent,to support its dominance.For example,in Yang et al.[23]only 6%of Co doping was sufficient to alter the magnetic phase of the Ni rod along with the change of microstructure from nano-crystalline to polycrystalline.In Telling et al.[35],Co was more magnetically dominant than Mn in Co 2MnAl,due to a smaller gap in the Co minority spin-band.Even in the theoretical work Wang et al.[36]pointed out that in a Cu–Co bimetallic clustersystem,Fig.6.Sum-rule (S z þL z )analyses for Ni,Fe,for x ¼0.3before and after the RTA treatment.The scale of the y -axis is selectively presented for the purpose ofclarity.Fig.7.(a)M –H curves (b)XRD patterns (c)Ni L 2,L 3XAS (d)Fe L 2,L 3XAS (e)Ni L 2,L 3XMCD and (f)Fe L 2,L 3XMCD,for x ¼0.5before and after the RTA treatment.In (b),Mix,Mix 0and Mix 00represent the three characteristic peaks of the BCC–FCC mixed phase just near the characteristic peaks of Cu,and these peaks are still observable after the RTA.S.-J.Chang et al./Journal of Magnetism and Magnetic Materials 332(2013)21–2726the introduction of Cu atoms would cause a dramatic enhance-ment of magnetism due to geometrical characters.All these phenomena suggest that,in a bimetallic system the physical proximity effects would lose balance if any two physical degrees of freedom of one constituent are more coupled than the other constituent.This will lead to the dominance of the constituent with the stronger coupling,if one of its degrees of freedom is elaborated.Assigning this principle to our case,we elaborate the structural instability to imbalance the physical proximity effect between Ni and Fe,which sharply discriminates the electronic responses of the two.Correlating the structural information with the local and macroscopic magnetism,it is easy to observe the dominance of Ni in Ni x Fe1Àx.Finally,the invariant magnetizations with the RTA for x¼0.3and0.5,therefore,need to be described by different microscopic pictures.For the former,it results from the spin exchange between Ni and Fe.However,the latter is char-acterized by the static,inactive interactions between the two elements as a result of the persistent structural stability.4.ConclusionIn this study we have demonstrated how Ni–Fe magnetic interactions influenced the Ni x Fe1Àx nano-wires’magneto-structural properties,by isolating the Ni and Fe elemental behaviors while the wires underwent the structural transition. The influences of the two elements were found to be incompar-able,with Ni being superior to Fe in terms of magnetic and structural properties.Upon RTA,the wires at x¼0.3became amorphous,where the Ni and Fe moments compensated mutually by exchanging the3d electrons.This reasoned the nearly unal-tered magnetization of the wires.A similar macroscopic behavior was seen at x¼0.5,while its invariant magnetization needed to be described as the inactive electronic interaction between the two elements,because of persistent structural properties resulting from a larger fraction of Ni.AcknowledgmentThe authors appreciate the assistances on HRTEM,XMCD,and electro-deposition from Dr.C.M.Liu,Dr.H.J.Lin and Mr.K.M. Chen,respectively.This work is supported by the National Science Council of Taiwan,under Grant no.NSC98-2112-M-009022-MY3. References[1]M.Kl¨aui,Journal of Physics:Condensed Matter20(2008)313001.[2]C.L.Dennis,R.P.Borges,L.D.Buda,U.Ebels,J.F.Gregg,M.Hehn,E.Jouguelet,K.Ounadjela,I.Petej,I.L.Prejbeanu,M.J.Thornton,Journal of Physics: Condensed Matter14(2002)R1175–262.[3]O.Yamada, cheisserie,Journal of the Physical Society of Japan53(1984)729–734.[4]E.F.Wassermann,Journal of Magnetism and Magnetic Materials100(1991)346.[5]B.Glaubitz,S.Buschhorn,F.Brussing,R.Abrudan,H.Zabel,Journal of Physics:Condensed Matter23(2011)254210.[6]B.Singh,C.L.Ho,Y.C.Tseng,C.T.Lo,Journal of Nanoparticle Research14(2012)706.[7]J.Crangle,G.C.Hallam,Proceedings of the Royal Society A272(1963)119.[8]R.F.Willis,N.J.Gilman,Europhysics Letters69(2005)411.[9]K.H.Lee,H.Y.Lee,W.Y.Jeung,W.Y.Lee,Journal of Applied Physics91(2002)8513.[10]A.Cai,H.Zhang,H.Hua,Z.Zhang,Nanotechnology13(2002)627.[11]M.S.Salem,P.Sergelius,R.Zierold,J.M.Montero Moreno,D.G¨orlitz,K.ielsch,Journal of Materials Chemistry22(2012)8549.[12]C.T.Chen,Y.U.Idzerda,H.J.Lin,N.V.Smith,G.Meigs,E.Chaban,G.H.Ho,E.Pellegrin,F.Sette,Physical Review Letters75(1995)152.[13]F.E.Atalay,H.Kaya,Journal of Alloys and Compounds469(2009)458.[14]S.Aravamudhan,J.Singleton,Journal of Physics D:Applied Physics42(2009)115008.[15]C.G.Wu,H.L.Lin,Journal of Solid State Electrochemistry10(2006)198.[16]H.R.Khan,K.Petrikowski,Journal of Magnetism and Magnetic Materials213(2000)526.[17]Q.Liu,J.Wang,Z.Yan,D.Xue,Physical Review B72(2005)144412.[18]F.Tain,J.Zhu,D.Wei,Journal of Physical Chemistry C111(2007)12699.[19]J.B.Wang,X.Z.Zhou,Nanotechnology15(2004)485.[20]Y.B.Zhu,Y.Wang,X.Y.Zhang,G.W.Qin,International Journal of RefractoryMetals and Hard Materials25(2007)275.[21]X.W.Wang,G.T.Fei,Journal of Physical Chemistry B109(2005)24326.[22]C.C.Huang,C.C.Lo,Y.C.Tseng,C.M.Liu,C.Chen,Journal of Applied Physics109(2011)113905.[23]C.Y.Yang,C.C.Huang,Y.C.Tseng,C.M.Liu,C.Chen,Journal of Applied Physics110(2011)073913.[24]C.Magen,L.Morellon,P.A.Algarabel,M.R.Ibarra,C.Ritter,A.O.Pecharsky,K.A.Gschneidner Jr.,V.K.Pecharsky,Physical Review B70(2004)224429.[25]D.Haskel,Y.B.Lee,B.N.Harmon,Z.Islam,ng,G.Srajer,Ya.Mudryk,K.A.Gschneidner Jr.,V.K.Pecharsky,Physical Review Letters98(2007) 247205.[26]//ox_potential.htm S.[27]E.Pellegrin,M.Hagelstein,S.Doyle,H.O.Moser,J.Fuchs, D.Vollath,S.Schuppler,M.A.James,S.S.Saxena,L.Niesen,O.Rogojanu,G.A.Sawatzky,C.Ferrero,M.Borowski,O.Tjernberg,N.B.Brookes,Physica Status Solidi(b)215(1999)797.[28]L.Signorini,L.Pasquini,F.Boscherini,E.Bonetti,I.Letard,S.Brice-Profeta,P.Saincavit,Nuclear Instruments and Methods in Physics Research Section B 246(2006)20.[29]W.C.Tsai,S.C.Liao,H.C.Hou,C.T.Yen,Y.H.Wang,H.M.Tsai,F.H.Chang,H.J.Lin,i,Applied Physics Letters100(2012)172414.[30]D.H.Kim,H.J.Lee,G.Kim,Y.S.Koo,J.H.Jung,H.J.Shin,J.-Y.Kim,J.-S.Kang,Physical Review B79(2009)033402.[31]All XMCD spectra presented in this work were normalized to the integrationsof corresponding XAS spectra,which was to guarantee the comparison based on an atomic absorption.[32]N.R.Khasanova, F.Izumi,M.Shida, B.C.Chakoumakos, E.Ohshima,M.Kikuchi,Syono,Physica C269(1996)115.[33]S.A.Bewick,R.A.Pascal,D.M.Ho,Z.G.Soos,M.Masino,Journal of ChemicalPhysics122(2005)024710.[34]M.Zhang,M.R.Anderson,Langmuir10(1994)2807.[35]N.D.Telling,P.S.Keatley,G.van der Laan,R.J.Hicken, E.Arenholz,Y.Sakuraba,M.Oogane,Y.Ando,K.Takanashi, A.Sakuma,T.Miyazaki, Physical Review B78(2008)184438.[36]J.Wang,G.Wang,X.Chen,W.Lu,J.Zhao,Physical Review B66(2002)014419.S.-J.Chang et al./Journal of Magnetism and Magnetic Materials332(2013)21–2727。
超导磁共振氦压缩机结构功能与故障案例分析
维修工程中国医学装备2024年4月第21卷第4期 China Medical Equipment 2024 April V ol.21 No.4Structural function and failure case analysis of superconducting magnetic resonance helium compressor/Zhang Falun 1, Wang Jixi 2, Zhou Yalin 2, Shi Zhan 31Department of Medical Equipment T eaching and Research, Jiangsu Health V ocation College, Nanjing 211800, China; 2Department of Medical Engineering, Jiangsu Province Official Hospital, Nanjing 210024, China; 3Siemens Medical Systems Ltd., Shanghai 201318, ChinaCorresponding author: [Abstract] Helium compressor is the core component of the refrigeration system of superconducting magnetic resonance imaging (MRI) equipment, and timely resolution of helium compressor failures is crucial to ensure the stability of the superconducting magnet cryogenic system. T aking the Sumitomo F-70 helium compressor manufactured by Sumitomo Heavy Industries as an example, the structural composition and functional principle of the helium compressor for superconducting MRI were analyzed, and the maintenance ideas and solutions for common helium compressor faults were proposed. By developing standardized fault maintenance strategies, reference was provided for failures of other types of helium compressor, so as to improve the quality of clinical technical support.[Key words] Superconducting magnetic resonance imaging; Helium compressor; Structure and function; Fault diagnosisFund program: 2022 Faculty Research Projects of Jiangsu Health V ocation College (JKC2022006)[摘要] 氦压缩机是超导磁共振成像(MRI)设备制冷系统核心部件,及时解决氦压缩机故障对保障超导磁体低温系统的稳定性至关重要。
开启片剂完整性的窗户(中英文对照)
开启片剂完整性的窗户日本东芝公司,剑桥大学摘要:由日本东芝公司和剑桥大学合作成立的公司向《医药技术》解释了FDA支持的技术如何在不损坏片剂的情况下测定其完整性。
太赫脉冲成像的一个应用是检查肠溶制剂的完整性,以确保它们在到达肠溶之前不会溶解。
关键词:片剂完整性,太赫脉冲成像。
能够检测片剂的结构完整性和化学成分而无需将它们打碎的一种技术,已经通过了概念验证阶段,正在进行法规申请。
由英国私募Teraview公司研发并且以太赫光(介于无线电波和光波之间)为基础。
该成像技术为配方研发和质量控制中的湿溶出试验提供了一个更好的选择。
该技术还可以缩短新产品的研发时间,并且根据厂商的情况,随时间推移甚至可能发展成为一个用于制药生产线的实时片剂检测系统。
TPI技术通过发射太赫射线绘制出片剂和涂层厚度的三维差异图谱,在有结构或化学变化时太赫射线被反射回。
反射脉冲的时间延迟累加成该片剂的三维图像。
该系统使用太赫发射极,采用一个机器臂捡起片剂并且使其通过太赫光束,用一个扫描仪收集反射光并且建成三维图像(见图)。
技术研发太赫技术发源于二十世纪九十年代中期13本东芝公司位于英国的东芝欧洲研究中心,该中心与剑桥大学的物理学系有着密切的联系。
日本东芝公司当时正在研究新一代的半导体,研究的副产品是发现了这些半导体实际上是太赫光非常好的发射源和检测器。
二十世纪九十年代后期,日本东芝公司授权研究小组寻求该技术可能的应用,包括成像和化学传感光谱学,并与葛兰素史克和辉瑞以及其它公司建立了关系,以探讨其在制药业的应用。
虽然早期的结果表明该技术有前景,但日本东芝公司却不愿深入研究下去,原因是此应用与日本东芝公司在消费电子行业的任何业务兴趣都没有交叉。
这一决定的结果是研究中心的首席执行官DonArnone和剑桥桥大学物理学系的教授Michael Pepper先生于2001年成立了Teraview公司一作为研究中心的子公司。
TPI imaga 2000是第一个商品化太赫成像系统,该系统经优化用于成品片剂及其核心完整性和性能的无破坏检测。
The Rice Convection Model(2020年整理).ppt
The reconnection model proposed by Dungey was validated by observation. It provided a physical mechanism that transform the magnetic energy into kinetic energy and thermal energy quickly.
➢ Its position is mainly controlled by magnetic pressure of magnetosheath and dynamical pressure of the solar wind.
Magnetic storms with sudden commencements (ssc) occurs when there are IMF shocks or discontinuities ( kinetic pressure of the solar wind increases suddenly), the magnetic field on the ground increases dozens of nTs because of the compression of the magnetopause.
• Phan et al.[2006] used the Geotail and Wind data during stable dawn ward dominated IMF to infer the presence of a tilted X line hinged near the sub-solar point.
• Magnetopause boundary (transition region into the magnetosphere)
《现代全身ct诊断学(第4版)》出版
国际医学放射学杂志IntJMedRadiol2020Jan 鸦43穴1雪Diagn,2016,36:1225-1232.[14]Khalili N,Lessmann N,Turk E,et al.Automatic brain tissue seg 鄄mentation in fetal MRI using convolutionalneural networks[J].Magn Reson Imaging,2019,DOI:10.1016/j.mri.2019.05.020.[15]Andescavage NN,du Plessis A,McCarter R,et plex Trajec 鄄tories of brain development in the healthy human fetus[J].Cereb Cor 鄄tex,2017,27:5274-5283.[16]Andescavage N,duPlessis A,Metzler M,et al.In vivo assessment ofplacental and brain volumes in growth -restricted fetuses with and without fetal Doppler changes using quantitative 3D MRI[J].J Peri 鄄natol,2017,37:1278-1284.[17]Ortinau CM,Mangin-Heimos K,Moen J,et al.Prenatal to postnataltrajectory of brain growth in complex congenital heart disease [J].Neuroimage Clin,2018,20:913-922.[18]Habas PA,Kim K,Rousseau F,et al.Atlas-based segmentation ofdeveloping tissues in the human brain with quantitative validation in young fetuses[J].Hum Brain Mapp,2010,31:1348-1358.[19]Dahdouh S,Limperopoulos C.Unsupervised fetal cortical surfaceparcellation[J].Proc SPIE Int Soc Opt Eng,2016,9784.pii:97840J.[20]Ortinau CM,Rollins CK,Gholipour A,et al.Early-emerging sulcalpatterns are atypical in fetuses with congenital heart disease [J].Cereb Cortex,2018,DOI:10.1093/cercor/bhy235.[21]Depping MS,Thomann PA,Wolf ND,et mon and distinctpatterns of abnormal cortical gyrificationin major depression and borderline personality disorder[J].Eur Neuro psychopharmacol,2018,28:1115-1125.[22]Barkhof F,Haller S,Rombouts SA.Resting -state functional MRimaging:a new window to the brain[J].Radiology,2014,272:29-49.[23]Marami B,Mohseni Salehi SS,Afacan O,et al.Temporal slice regis 鄄tration and robust diffusion-tensor reconstruction for improved fetal brain structural connectivity analysis[J].Neuroimage,2017,156:475-488.[24]刘海东,许相丰.扩散加权成像在胎儿脑发育中的应用进展[J].国际医学放射学杂志,2016,39:378-381.[25]Song L,Mishra V,Ouyang M,et al.Human fetal brain connectome:structural network development from middle fetal stage to birth [J].Front Neurosci,2017,11:561.[26]Song JW,Gruber GM,Patsch JM,et al.How accurate are prenataltractography results?A postnatal in vivo follow-up study using diffu 鄄sion tensor imaging[J].Pediatr Radiol,2018,48:486-498.[27]van den Heuvel MI,Thomason ME.Functional connectivity of thehuman brain in utero[J].Trends Cogn Sci,2016,20:931-939.[28]Hoinkiss DC,Erhard P,Breutigam NJ,et al.Prospective motion cor 鄄rection in fynctional MRI using simultaneous multislice imaging and multislice-to-volume image registration[J].NeuroImage,2019,200:159-173.[29]van den Heuvel MI,Turk E,Manning JH,et al.Hubs in the humanfetal brain network[J].Dev Cogn Neurosci,2018,30:108-115.[30]Wu W,Mcanulty G,Hamoda HM,et al.De tecting microstructuralwhite matter abnormalities of frontal pathways in children with AD 鄄HD using advanced diffusion models[J].Brain Imaging Behav,2019,DOI:10.1007/s11682-019-00108-5.[31]Jakab A,Schwartz E,Kasprian G,et al.Fetal functional imagingportrays heteroge neous development of emerging human brain net 鄄works[J].Front Hum Neurosci,2014,8:852.[32]Batalle D,Mu 觡oz-Moreno E,Tornador C,et al.Altered resting-statewhole -bra in functional networks of neonates with intrauterine growth restriction[J].Cortex,2016,77:119-131.[33]Wheelock MD,Hect JL,Hernandez -Andrade E,et al.Sex differ 鄄ences in functional connectivity during fetal brain development [J].Dev Cogn Neurosci,2019,36:100632.(收稿2019-04-25)唐光健、秦乃姗教授主编的《现代全身CT 诊断学(第4版)》已由中国医药科技出版社出版。
Correlations among magnetic, electrical and magneto-transport properties of NiFe nanohole arrays
Home Search Collections Journals About Contact us My IOPscienceCorrelations among magnetic, electrical and magneto-transport properties of NiFe nanohole arraysThis article has been downloaded from IOPscience. Please scroll down to see the full text article.2013 J. Phys.: Condens. Matter 25 066007(/0953-8984/25/6/066007)View the table of contents for this issue, or go to the journal homepage for moreDownload details:IP Address: 202.207.14.58The article was downloaded on 12/03/2013 at 07:46Please note that terms and conditions apply.IOP P UBLISHING J OURNAL OF P HYSICS:C ONDENSED M ATTER J.Phys.:Condens.Matter25(2013)066007(9pp)doi:10.1088/0953-8984/25/6/066007Correlations among magnetic,electrical and magneto-transport properties of NiFe nanohole arraysD C Leitao1,J Ventura2,J M Teixeira2,C T Sousa2,S Pinto2,J B Sousa2,J M Michalik3,4,5,J M De Teresa3,4,5,M Vazquez6and J P Araujo21INESC-MN and IN,Rua Alves Redol9,1000-029Lisboa,Portugal2IFIMUP and IN,Departamento de F´ısica e Astronomia,Faculdade de Ciˆe ncias da Universidade doPorto,Rua do Campo Alegre,678,4169-007,Porto,Portugal3Instituto de Ciencia de Materiales de Aragon(ICMA),CSIC—Universidad de Zaragoza,E-50009Zaragoza,Spain4Laboratorio de Microcopias Avanzadas(LMA),Instituto de Nanociencia de Arag´o n(INA),Universidad de Zaragoza,E-50018Zaragoza,Spain5Departamento de F´ısica de la Materia Condensada,Universidad de Zaragoza,E-50009Zaragoza,Spain6Instituto de Ciencia de Materiales de Madrid CSIC,E-28049Madrid,SpainE-mail:dleitao@inesc-mn.ptReceived8August2012,infinal form17December2012Published11January2013Online at /JPhysCM/25/066007AbstractIn this work,we use anodic aluminum oxide(AAO)templates to build NiFe magneticnanohole arrays.We perform a thorough study of their magnetic,electrical andmagneto-transport properties(including the resistance R(T),and magnetoresistance MR(T)),enabling us to infer the nanoholefilm morphology,and the evolution from granular tocontinuousfilm with increasing thickness.In fact,different physical behaviors were observedto occur in the thickness range of the study(2nm<t<100nm).For t<10nm,aninsulator-to-metallic crossover was visible in R(T),pointing to a granularfilm morphology,and thus being consistent with the presence of electron tunneling mechanisms in themagnetoresistance.Then,for10nm<t<50nm a metallic R(T)allied with a largeranisotropic magnetoresistance suggests the onset of morphological percolation of the granularfilm.Finally,for t>50nm,a metallic R(T)and only anisotropic magnetoresistance behaviorwere obtained,characteristic of a continuous thinfilm.Therefore,by combining simplelow-cost bottom-up(templates)and top-down(sputtering deposition)techniques,we are ableto obtain customized magnetic nanostructures with well-controlled physical properties,showing nanohole diameters smaller than35nm.(Somefigures may appear in colour only in the online journal)1.IntroductionThe introduction of voids into a thinfilm significantly alters the characteristics of the medium,leading to exotic and interesting physical properties.In fact,such voids can lead to quantum effects in the conductivity[1,2],enhanced optical transmission[3],artificial vortex pinning sites in superconductors[4]and magnonic crystals[5,6],facilitating research and technological applications.Regarding magnetic materials,the inclusion of these artificial defects becomes an easy way to engineer their properties at micrometer and nanometer scales[7,8].The voids alter the stray field distribution(compared to a continuousfilm)and pin domain walls(DWs),thus influencing the coercivity and remanence[9,10]while at the same time tailoring the magnetization switching processes[11].Therefore,nanoholeFigure 1.AFM images of the (a)as-grown AAO substrate and (b)25nm thick NiFe nanohole array.arrays embedded in a magnetic thin film have been pointed out as a promising route to obtaining future data storage media [7].The main advantage of these structures resides in the absence of the superparamagnetic limit for small bit size,since there is no isolated magnetic volume.Nowadays,researchers focus mainly on understanding the physical properties of nanohole arrays with nanometer dimensions,where the magnetic domain morphology and reversal processes are very much distinct from those of the widely studied micrometer-period structures [11–15].Studies on exchange-biased systems provide an example where the inter-hole distance (D int )and hole diameter (D h )can be comparable to the characteristic domain lengths of the ferromagnetic and/or antiferromagnetic layers [16,17].Nevertheless,the main challenge regarding such nm-size arrays still lies in the fabrication processes.Most of the published works rely on lithography-based processes such as electron-beam and lift-off [7],focused-ion-beam [16]and deep ultraviolet [18]methods.As an alternative,one may chose a bottom-up approach consisting of self-assembly procedures [19–21].One reliable method resorts to anodic aluminum oxide (AAO)as a pre-patterned substrate for template-assisted growth of the nanohole arrays,with major advantages regarding process simplicity and cost [12,13,9,22,23].In this work,we study in detail the magnetic,electrical and magneto-transport properties of NiFe nanohole arrays with thicknesses (t )ranging from 2to 100nm,sputter deposited on top of AAO.NiFe is a well-characterized alloy,with extensive literature concerning the magnetic and transport properties for continuous thin films and micrometer-size nanohole arrays.It provides an excellent starting point for addressing different physical aspects such as the morphology of thin films grown on top of nanopatterned and rough substrates such as AAO templates.In addition,NiFe is also relevant in a wide number of applications ranging from motor cores to magnetic recording [24,25].Using temperature dependent resistance (R (T ))and magnetoresistance (MR (T ))measurements together with room temperature magnetic characterizations (M (H )),we were able to address the morphology of the NiFe nanohole array.An evolution from an island-like morphology towards a continuous thin film with increasing t was observed.Also,Hall resistivity (ρH )measurements show an increase of the planar Hall effectcontribution with thickness,here ascribed to the in-plane magnetic anisotropy induced during growth.2.Experimental detailsFor the growth of magnetic nanohole arrays we used anodic aluminum oxide (AAO)templates obtained by a standard two-step method of anodization of high-purity (99.997%)Al foils [26].After an electropolishing pre-treatment,the Al foils were anodized in a 0.3M oxalic acid solution at ∼4◦C and under an applied potential of 40V [27].The first anodization was carried out for 24h while the second lasted 1h.These anodization conditions resulted in nanopores disposed in an ordered hexagonal lattice (figure 1(a)),with an average diameter of ∼35nm,separation of ∼105nm and length of ∼2.5µm.On top of the AAO we deposited a NiFe (80:20)thin film using a 1160L four-target ion-beam deposition (IBD)system from Commonwealth Scientific Corporation with a base pressure of ∼8×10−7Torr [28].A beam voltage of 1000V and a beam current of 15mA were used,giving a NiFe deposition rate of 0.035nm s −1for an Ar flow of 5sccm with the working pressure of ∼2×10−4Torr.During deposition a magnetic field of 250Oe was applied in the sample plane,inducing an uniaxial magnetic easy axis.We varied the nominal thickness (t )of the NiFe thin films within the 2nm ≤t ≤100nm range.Continuous control samples were also deposited on Si/SiO 2substrates in the same batch.The surface of the samples was analyzed with a low-vacuum FEI Quanta 400FEG scanning electron microscope (SEM)and a nanoscope multimode atomic force microscope (AFM)from Veeco Instruments operating in tapping mode.Magnetic characterization was performed with a commercial VSM magnetometer (KLA-Tencor EV7VSM)at room temperature.The measurements were performed with the magnetic field applied in the sample’s plane,both parallel ( )and transverse (⊥)to the uniaxial direction induced during growth.In addition,temperature dependent magnetic properties (M (T ))were also studied with a Quantum Design SQUID magnetometer (5–350K)and the zero-field-cooled/field-cooled (ZFC/FC)curves were measured with a field (H )of 50Oe applied along the growth-induced uniaxial direction.The R (T )and MR (T )measurements were performed with a pseudo-four-probe DC method from 20Figure2.(a)Average D h dependence on t showing a quasi-linear trend.(b)Gaussian distribution of D h sizes for the nanohole sample with t=30nm.SEM top-surface images of(c)AAO and(d)a30nm thick nanohole array.to300K and applied magneticfields up to6kOe.The MR properties were characterized in the longitudinal( ) and transverse(⊥)geometries(with magneticfield always applied in the sample’s plane)and the currentflowing parallel to the induced uniaxial direction.Electrical contacts were placed on the sides of the samples enclosing the width of the nanohole arrays,and defined by sputtering using a shadow mask.ForρH measurements,the samples were patterned by optical lithography into a well-defined geometry,consisting of a300µm electrode where currentflows,sided with pads for the measurement of voltage drop,and this allows one to minimize offset voltages in the Hall measurements[29].3.Experimental results3.1.Morphology of the nanohole arraysFigure1compares AFM topography images of the AAO substrate and a25nm thick NiFe nanohole array.As expected, the AAO hexagonal pattern is replicated by the thinfilm deposited on top.The latter grows mainly on the surface between the nanopores,giving rise to holes embedded in the continuousfilm[12,22].Furthermore,six hills(height of ∼10–15nm)surrounding each nanopore are also replicated by the coveringfilm.Figure2(a)displays the dependence of the hole diameter (D h)on the thickness(t)of the depositedfilm obtained from statistical analysis of SEM images(figures2(c)and (d)).For low t,the magneticfilm retains the size of the nanopores underneath;however,with increasing t,the hole diameter is reduced until a continuousfilm is formed.In fact,a quasi-linear D h(t)dependence is observed and a critical thickness of t c≈52nm can be extrapolated for the closure of the nanopores.The latter occurs due to deposition of material around the pore entrance which progressively leads to its closure.In fact,Rahman et al observed that for high-aspect-ratio AAO(like that used here),deposition occurs only on the top surface of the template[11,15].In addition,cross-section images revealed,in particular,closing of pores with conical-like features lying within the nanopore entrances[12–14].3.2.Magnetic propertiesFigure3shows the room temperature M(H)behavior for selected nanohole arrays and corresponding continuous thin films(t=2,30and100nm).The continuousfilms show a squared easy-axis M(H)loop consistent with DW nucleation and propagation,while an almost linear M(H)is observed for the hard axis,ascribed to magnetization rotation(figures 3(a2)–(c2))[12].In contrast,the nanohole arrays display an almost isotropic M(H)behavior with an overall increase in coercivity(H c)and decrease in remanence(m r)(figures 3(a1)–(c1))[9,30],as predicted by the inclusion theory[31]. The inset offigure3(b1)displays the angular dependence of H c for the t=30nm sample.H c(θ)reveals a small change (∼4Oe)between the(expected growth-induced)easy and hard axes.In this case,the substantial roughness and particular topography of the AAO substrates are crucial and may lead to irregular growth of the magneticfilm,thus smearing theFigure3.Room temperature M(H)curves for nanohole arrays and corresponding continuous thinfilms with(a)t=2nm(thin),(b)t=30nm(intermediate)and(c)t=100nm(thick).Note the distinct magneticfield magnitudes of the nanohole and thinfilm samples. The and⊥symbols correspond to the direction of H relative to the growth-induced axis.The inset of(a1)shows a widefield range ofM(H)for the2nm sample.The inset of(b1)shows the angular dependence of H c for30nm nanohole arrays.definition of an average preferential magnetic direction[32]. Since a hexagonal multidomain[27]hole structure is present in these AAO cases,no clear influence from the underlying lattice is observed in M(H).Notice the particular M(H)shape for nanohole samples with t=30and100nm.When thefield reverses (figure3(c1)),we observe an abrupt jump of M(H) characteristic of DW motion;the magnetic moments are therefore reversed in the continuous zones between holes.However,at sites where the anisotropy is stronger (surrounding the holes;accentuated hills),the spins still show an angle relative to H.With further H increase a smoother M(H)behavior approaching magnetic saturation is seen.Such behavior was previously predicted[32],but never observed.In contrast,the thinner sample(t=2nm)shows an M(H)behavior resembling that of nanogranular systems (figure3(a1))[33,34],with H ,⊥c 80Oe,whereas for100nm samples an H ,⊥c 15Oe was obtained instead.Furthermore,an increase in m r with t is visible for the nanohole arrays.This effect is a consequence of the stray fields arising from the dipoles around the nanoholes,and becomes increasingly important for reducing thickness.The inclusion of a small percentage offilm around the entrance of the nanopores also leads to reduced in-plane H c and m r[32,35],due to the appearance of a small out-of-plane magnetization component.3.3.Transport propertiesFigure4shows normalized R(T)curves for selected nanohole arrays(t=2,6,100nm)representative of the entire deposited thickness range.For t<10nm,a pronounced minimum is visible in R(T)at temperatures(T∗)of130and65K for t=2 and6nm,respectively.Above T∗a metallic-like behavior is present(d R/d T>0),while below T∗an insulator-like R(T) characterized by d R/d T<0is obtained.In particular,theFigure 4.R (T )curves for selected nanohole array samples and corresponding continuous thin films with values of t of (a)2nm,(b)6.5nm and (c)100nm.(d)Sheng–Abeles law fit to the insulator R (T )part of the nanohole array with t =2nm.The inset of(c)shows the ZFC–FC M (T )curve for the nanohole array sample with t =2.8nm.insulator part of R (T )for the nanohole array with t =2nm follows the Sheng–Abeles law [36](figure 4)expected for discontinuous films [33,36–38],R =R 0exp 2Ck B T 1/2,where C and k B are the activation energy and Boltzmann constants,respectively.A rather low Sheng–Abeles activation energy of C =7.6×10−3meV was obtained from our results.We note that in CoFe (t )/Al 2O 3discontinuous multilayers,activation energies ranging from ∼0.1meV for t =1.6nm to ∼8meV for t =1.2nm were found [33,37].The first value was obtained for samples close to morphological percolation and displaying an insulator R (T )behavior over the entire measurement temperature range (20–300K).Interestingly,the sample with t =2nm displayed an R (T )behavior similar to the one presented here,although no values of C were given for this case [33].The observed transition from tunnel to metallic-like transport suggests that these thinner samples are composed of tunnel bridges connecting continuous magnetic clusters of large size,the latter being part of a metallic network within the NiFe nanohole array.Additional ZFC/FC curvesfor a nanohole array with t =2.8nm display a bifurcation at low temperatures (∼162K),characteristic of materials with large magnetic anisotropies and consistent with island-like morphologies.Furthermore,two mean blocking temperatures (T B )of ∼29and ∼120K are observed,indicating the presence of a distinctive size distribution for magnetic domains,as suggested from transport measurements.On the other hand,for t ≥10nm a typical metallic R (T )is observed for the nanohole arrays.In particular,the R (T )behavior is similar for t =100nm thin film and nanohole samples,corroborating our hypothesis that the holes start to close and the samples approach the (continuous)thin film condition.Figure 5shows the MR behavior at 100K for the same set of samples (t =2,6and 100nm).Here,we define the MR ratio asMR ,⊥=R (H )−R (H max )R (H max ),where H max is the maximum applied field (=6kOe).Overall,the measured values of MR are consistently smaller than for the corresponding continuous samples.Such an accentuated decrease originates mainly from the nanoholes introduced,which confine and locally alter the electrical current paths [18,32].Notice that the thinner sample (t =2nm)displays an almost isotropic MR behavior,with similar magnitudes for the two H configurations (figures 5(a)and (b)).This triangular shape curve is typically observed for systems of discontinuous magnetic multilayers and attributed to the presence of TMR [33,39](‘T’standing for tunnel).Such a contribution is further corroborated by the crossover between insulator and metallic transport observed in R (T )(figure 4(a)).Moreover,and although no distinguishable peaks are visible near the origin,the sharper feature at H =0in MR may be a consequence of easier magnetization reversal due to a reminiscent growth-induced magnetic anisotropy,mainly in regions where large magnetic clusters are present.Figure 6(b)displays the Hall resistivity (ρH )measurements for the t =2nm nanohole array sample.In this case,a planar Hall effect contribution is observed in ρH ,consistent with the presence of an in-plane magnetization component.With increasing t an in-plane AMR (‘A’standing for anisotropic)behavior is observed (figures 5(c)–(f))[8],in agreement with the larger planar Hall effect contribution observed for t =100nm,as compared with t =2nm (figure 6(d)).For such a thickness range,the MR curves display two peaks at low fields ascribed to the switching field of the magnetization (H sw ),followed by an almost linear MR dependence at moderate fields (0.5kOe <H <6.0kOe).This particular MR shape indicates the presence of two reversal mechanisms [12]:the peaks are consistent with DW displacement occurring in the continuous space between the nanoholes.In contrast,the linear MR is characteristic of a non-homogeneous rotation of the magnetic moments closer to the edges of the holes [22].Such misalignment of the magnetic moments relative to the external magnetic field is directly related to the particular topography of the filmgeometries.The insets show details near H sw.Figure6.(a)Optical image of the sample used to measureρH.Room temperatureρH for(b)t=2nm and(c)t=100nm nanohole arrays.(d)Comparison between the shapes of the twoρH signals;due to the differentρH magnitudes,the data were normalized.For magneticmaterials,ρH=R Oµ0H+R Aµ0M,the ordinary Hall effect being proportional to H and the anomalous Hall effect,to the out-of-plane M.induced by the underlying substrate(embedded holes and hills surrounding each hole)[40].We would also like to remark that for t=100nm, two bumps appear close to H=0(figures5(e)and(f)). Similar features were observed in the out-of-plane MR curves[41],confirming the presence of a local out-of-plane magnetization component,probably resulting from material deposited around the entrance of the nanoholes,or from the pronounced AAO topography mimicked by thefilm.4.DiscussionThe resistivity(ρ)value at afixed temperature is usually an easy and straightforward parameter to extract as a figure of merit for a sample’s properties.However,the particular geometry of an array of nanoholes makes such afigure of merit hard to obtain.The holes,together with the complex topography of the AAO and the changes in thefilm morphology with increasing thickness,lead to an extraordinarily complex interpretation being required to reliably obtain a cross-sectional area and an effective current path between electrical contacts for each sample.In analogy,one can introduce a pseudo-resistivity parameter (ρ∗),obtained fromρ∗=R wtL,(1) where R is the measured resistance,t(w)is the thickness (width)of thefilm and L is the spacing between the electrical contacts.ρ∗relates to the realρof the nanoholefilm system throughρ=F(w,t,L)ρ∗,where F represents a form factor (effective cross-sectional area and electrical contact distance) correlated with thefilm morphology.Figure7(a)shows the room temperatureρ∗(t)depen-dence for the nanohole array samples.Initially,ρ∗(t)has a similar trend to the continuous thinfilms,decreasing rapidly as t increases(inset offigure7(a))[28,42]. However,a minimum is visible around t 50nm,which is close to our extrapolated thickness for the closure of the nanopores(figure2(a)).In contrast to the case for NiFe continuousfilms,a change in the effective(conductive) cross-section and current paths of these samples is expected as thefilm approaches the continuous regime,modulated by the underlying AAO topography.We emphasize that the anomalous increase visible inρ∗above50nm is not directly related to a higher intrinsic resistivity of the material,but more probably to complicated geometrical features arising as the nanohole closes,which are reflected in F(w,t,L)[13,14].Figure7(b)shows MR⊥(t)for the nanohole arrays at 100and300K.For a homogeneous and continuous thin film one obtains a monotonic increase of MR⊥(t),towards an almost constant value(inset offigure7(a)).However, for the nanohole samples,a completely different trend is observed(figure7(b)).First,an increase of MR⊥from2to 10nm is visible,which is then followed by a decrease up to t<50nm;finally an increase is again observed.Such behavior is inconsistent with the presence of only AMR for t<50nm.In fact,Krzyk et al systematicallystudied Figure7.(a)ρ∗and(b)MR⊥dependence on t for the nanohole arrays.The inset showsρ(t)and MR⊥(t)for the continuous NiFe thinfilms.The lines are guides to the eye.continuous ultrathin NiFefilms(0.5<t<4.5nm)deposited on different substrates(SiO2,MgO and Al2O3),where a competition between TMR and AMR contributions to the total MR(t)of the systems was present[43].Furthermore,the onset of AMR dominance depended on the nature of the substrate (t 1.8nm for Si/SiO2,t 3.8nm for MgO and t 5.6nm for Al2O3).Our data then suggest:(i)For t≤3nm the transport properties indicate the pres-ence of a significant tunnel contribution,corroborated by the insulator/metallic crossover observed in R(T)at low temperatures(figure4(a)).Furthermore,for the t= 2nm nanohole arrays,the data closely follow the ln R∝2(C/k B T)1/2dependence observed in granular systems and characteristic of the limit of low electricfield for tunneling(figure4).The almost isotropic MR behavior observed infigures5(a)and(b),together with the lack of distinguishable H sw peaks,is expected if thefilm is composed by islands of magnetic material[39].These characteristics point to a granular morphology,facilitated by the accentuated topography of the underlying AAO substrate,which in turn explains the particular M(H) behavior(figure3(a)).The NiFe nanohole array sample is then composed of tunnel bridges connecting continuous parts of a metallic network(i.e.ordered magnetic clusters of large size)[33].(ii)In the3nm<t≤10nm range,a remanent tunnel contribution is still present,as indicated by the insulator-like behavior observed in R(T)at very low temperatures.Nevertheless,a contribution from the AMR starts to appear,as supported by the visible changes in the shape of the MR(H)cycles(figures5(c)and(d)).(iii)For10nm<t≤50nm,a negligible contribution from the TMR is expected as the morphological percolation is largely overcome.Therefore,in this regime,MR(t) suggests the presence of a larger AMR effect in detriment to the TMR.Also,an entirely continuousfilm covering the space in between the nanoholes over the AAO surface is expected.(iv)Finally for t>50nm only the AMR is present.MR increases with t,following the same tendency as for thin films[28,42].The fact that MR⊥shows a particular dependence on t, suggesting the presence of TMR and AMR contributions,is here attributed to the substrate dependent growth morphology of thefilm,and thus of the nanohole arrays.5.ConclusionsWe observed that NiFe thinfilms deposited on top of AAO conform to its surface,reproducing the underlying hexagonal pattern.In addition,the pronounced topography of the AAO characterized by the presence of hills surrounding each nanopore was also transferred to the nanohole array.By correlating the magnetic,electrical and magneto-transport properties of the nanohole arrays,we inferred the nanoholefilm morphology,which depended strongly on the depositedfilm thickness and particular AAO topography. For small t a granular-likefilm is formed,promoted by the high roughness and the particular topography of the AAO substrates(figure1(a)).With increasing t,morphological percolation occurs and the contribution from TMR decreases. Therefore,when thefilm coalesces and the bulk-like part starts to dominate the conduction mechanisms,the TMR vanishes and only AMR is present.Interestingly,this coincides with the t value( 50nm)obtained for the closure of the nanopores.This work opens new doors to the growth of more complex nanostructured materials on AAO substrates obtained from the anodization of thick Al foils,with well-controlled physical properties,the latter being a crucial aspect for facilitating further technological advances. AcknowledgmentsThe authors thank Dr Andre M Pereira for valuable discussions concerning the manuscript.The work was supported in part by project FEDER/POCTI/n2-155/94. DCL,CTS and JMT are grateful for FCT grants (SFRH/BPD/72359/2010,SFRH/BD/82010/2011and SFRH/BPD/72329/2010).M Vazquez thanks the Spanish Ministry of Economia y Competitividad,MEC,for assistance under project MAT2010-20798-C05-01.References[1]Nakanishi T and Ando T1996Quantum interference effects inantidot lattices in magneticfields Phys.Rev.B548021[2]Uryu S and Ando T1998Numerical study of localization inantidot lattices Phys.Rev.B5810583[3]Ruan Z and Qiu M2006Enhanced transmission throughperiodic arrays of subwavelength holes:the role oflocalized waveguide resonances Phys.Rev.Lett.96233901 [4]Van de V ondel J,de Souza Silva C C,Zhu B Y,Morelle M andMoshchalkov V V2005V ortex-rectification effects infilmswith periodic asymmetric pinning Phys.Rev.Lett.94057003[5]Neusser S and Grundler D2009Magnonics:spin waves on thenanoscale Adv.Mater.212927–32[6]Neusser S,Botters B and Grundler D2008Localization,confinement,andfield-controlled propagation of spin wavesin Ni80Fe20antidot lattices Phys.Rev.B78054406[7]Cowburn R P,Adeyeye A O and Bland J A C1997Magneticdomain formation in lithographically defined antidotPermalloy arrays Appl.Phys.Lett.702309–11[8]Adeyeye A O,Bland J A C and Daboo C1997Magneticproperties of arrays of holes in Ni80Fe20films Appl.Phys.Lett.703164–6[9]Barnard J A,Fujiwara H,Inturi V R,Jarratt J D,Scharf T W and Weston J L1996Nanostructured magneticnetworks Appl.Phys.Lett.692758–60[10]Wang C C,Adeyeye A O,Singh N,Huang Y S andWu Y H2005Magnetoresistance behavior of nanoscaleantidot arrays Phys.Rev.B72174426[11]Rahman M T,Dumas R K,Eibagi N,Shams N N,Wu Y-C,Liu K and Lai C-H2009Controlling magnetization reversalin Co/Pt nanostructures with perpendicular anisotropy Appl.Phys.Lett.94042507[12]Merazzo K J,Leitao D C,Jimenez E,Araujo J P,Camarero J,del Real R P,Asenjo A and Vazquez M2011Geometry-dependent magnetization reversal mechanism inordered Py antidot arrays J.Phys.D:Appl.Phys.44505001 [13]Xiao Z L et al2002Nickel antidot arrays on anodic aluminasubstrates Appl.Phys.Lett.812869–71[14]Navas D,Ilievski F and Ross C A2009CoCrPt antidot arrayswith perpendicular magnetic anisotropy made on anodicalumina templates J.Appl.Phys.105113921[15]Tofizur Rahman M et al2008A large-area mesoporous arrayof magnetic nanostructure with perpendicular anisotropyintegrated on Si wafers Nanotechnology19325302 [16]Kovylina M,Erekhinsky M,Morales R,Villegas J E,Schuller I K,Labarta A and Batlle X2009Tuning exchangebias in Ni/FeF2heterostructures using antidot arrays Appl.Phys.Lett.95152507[17]Rahman M T,Shams N N,Wang D S and Lai C-H2009Enhanced exchange bias in sub-50-nm IrMn/CoFenanostructure Appl.Phys.Lett.94082503[18]Wang H,Wu Y,Wang M,Zhang Y,Li G and Zhang L2006Fabrication and magnetotransport properties of orderedsub-100nm pseudo-spin-valve element arraysNanotechnology171651[19]Ho C-C,Hsieh T-W,Kung H-H,Juan W-T,Lin K-H andLee W-L2010Reduced saturation magnetization in cobaltantidot thinfilms prepared by polyethylene oxide-assistedself-assembly of polystyrene nanospheres Appl.Phys.Lett.96122504[20]Zhukov A A,Goncharov A V,de Groot P A J,Bartlett P N and Ghanem M A2003Magnetic antidotarrays from self-assembly template methods J.Appl.Phys.937322–4[21]Wei Q,Zhou X,Joshi B,Chen Y,Li K-D,Wei Q,Sun K andWang L2009Self-assembly of ordered semiconductornanoholes by ion beam sputtering Adv.Mater.212865–9 [22]Leitao D C,Ventura J,Pereira A M,Sousa C T,Moreira J M,Carpinteiro F C,Sousa J B,Vazquez M andAraujo J P2010Study of nanostructured array of antidotsusing pulsed magneticfields J.Low Temp.Phys.159245–8。
药学英语Unit two-text A
15
biological macromolecules.
• The identity of each organism is preserved by its
possession of distinctive sets of nucleic acids and of proteins. • 所有的生命有机体都具有相同种类的单聚体;在 生物大分子的构成上采用基本的模式;每一种生
• enzyme 酶
6
• The molecules of which living organisms are composed conform to all the familiar laws of chemistry. • 组成生命有机体的分子都遵循着熟知的化学规律 • ,but they also interact with each other in accordance with another set of principles, which we shall refer to collectively as the molecular logic of life. • 但是这些分子却按照另一套规律相互作用,就是 我们将提到的生命的分子逻辑学的全部原理
?人类精子和卵子携带着数百万年进化累积的遗传信息以dna分子的形式传递着这些指令在dna分子中共价连接的核苷酸亚单位的线性序列编码着这些遗传信息
Unit Two
Text A Foundation of Biochemistry
1
biochemistry 生物化学
• carbon 碳
• hydrogen 氢
Method and apparatus for the reproduction of magne
专利名称:Method and apparatus for the reproductionof magnetically stored information发明人:WOIKE, THEO, DR.,KERKMANN,DETLEF,BEIER, THOMAS,KRASSER,WOLFGANG, DR.,PESCIA, DANILO, DR.申请号:EP90104874.4申请日:19900315公开号:EP0387866A2公开日:19900919专利内容由知识产权出版社提供专利附图:摘要:The invention relates to a method and an apparatus for the reproduction ofmagnetically stored information, in particular binary information, of a magnetooptical or optoelectronic storage medium. In this case it is the object of the invention to develop a method and an apparatus which are simple, compact and highly sensitive, and in particular allow the characterisation of storage layers with layer thicknesses down to mono-layers. The object of the invention is achieved by a method in which the items of information of the storage medium which are stored perpendicularly to the reflection plane are utilised. To do so, the electric signal of the photoelectric detector is reduced by a fixed value and subsequently suitably amplified electronically. The value is chosen here such that the fluctuations in the electric signal achieved due to the variation of the magnetic field are sensed. In the case of a particularly advantageous variant of the claimed method and of the claimed apparatus, a polariser is used, which is provided between storage medium and detector. In this arrangement, the polariser essentially absorbs that component of the light beam coming from the storage medium which does not contribute to determining the magnetic information contained in the storage medium. ……申请人:FORSCHUNGSZENTRUM JUELICH GMBH地址:WILHELM-JOHNEN-STRASSE; D-5170 JUELICH,Wilhelm-Johnen-Strasse D-52425 Jülich DE国籍:DE更多信息请下载全文后查看。
复合还原辅酶 生命源动力
复合还原辅酶生命源动力英文回答:Coenzyme is a molecule that plays a crucial role in various biochemical reactions in living organisms. One type of coenzyme is called a cofactor, which is a non-protein molecule that binds to an enzyme and helps it carry out its function. One example of a cofactor is NAD+ (nicotinamide adenine dinucleotide), which is involved in redox reactions in cells. NAD+ accepts electrons from one molecule and transfers them to another, thus facilitating the transfer of energy in the form of electrons. Another example is ATP (adenosine triphosphate), which is often referred to as the "energy currency" of the cell. ATP stores and releases energy during cellular processes, such as muscle contraction and active transport.In addition to cofactors, there are also coenzymes that are derived from vitamins. These coenzymes are called "vitamins in disguise" because they are modified versionsof vitamins that have been converted into their active forms. One example is coenzyme A (CoA), which is derived from vitamin B5 (pantothenic acid). CoA is involved in various metabolic reactions, including the breakdown of carbohydrates, fats, and proteins. It acts as a carrier molecule, transferring acetyl groups from one reaction to another. Without CoA, these metabolic pathways would not be able to function properly.The concept of "life force" or "life energy" is often associated with the idea of complex coenzymes. These coenzymes, such as NADH (the reduced form of NAD+) and FADH2 (the reduced form of flavin adenine dinucleotide), are involved in the process of cellular respiration. Cellular respiration is the process by which cells convert glucose and oxygen into carbon dioxide, water, and ATP. During this process, NADH and FADH2 donate electrons to the electron transport chain, which generates a proton gradient across the inner mitochondrial membrane. This proton gradient is then used by ATP synthase to produce ATP, the primary source of energy for cellular activities.In conclusion, complex coenzymes play a vital role in the energy metabolism of living organisms. They act as cofactors and carriers, facilitating biochemical reactions and the transfer of energy in the form of electrons. Coenzymes derived from vitamins, such as CoA, are essential for the breakdown of macronutrients. Moreover, coenzymes like NADH and FADH2 are involved in cellular respiration, the process that generates ATP, the "life force" of the cell.中文回答:辅酶是一种在生物体内各种生化反应中起着关键作用的分子。
无关言语影响老年人阅读过程的眼动研究
收稿日期:2020–12–07 * 基金项目:天津市哲学社会科学规划项目(TJJX17-009)。 通讯作者:吴 捷,E-mail:babaluosha@。
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Magneto-capacitance probing of the many-particle states in InAs dots Oliver S. Wibbelhoff1, Axel Lorke1, Dirk Reuter2, and Andreas D. Wieck21Institute of Physics, Universität Duisburg-Essen, Lotharstr. 1, D-47048 Duisburg, Germany2Solid State Physics, Ruhr-Universität Bochum, Universitätsstr. 150, D-44780 Bochum, GermanyWe use frequency-dependent capacitance-voltage spectroscopy to measure the tunneling probability into self-assembled InAs quantum dots. Using an in-plane magnetic field of variable strength and orientation, we are able to obtain information on the quasi-particle wave functions in momentum space for 1 to 6 electrons per dot. For the lowest two energy states, we find a good agreement with Gaussian functions for a harmonic potential. The high-energy orbitals exhibit signatures of anisotropic confinement and correlation effects.Tunneling spectroscopy is a well-known tool for the de-termination of quantized energies. Recently, it has also be-come possible to use this technique to directly study thewave function associated with an energy level. Using scan-ning tunneling microscopy (STM), it has been possible to observe the charge densities in structures like the quantumcorral1, image standing wave patterns with cross-sectionalSTM2 or to map out the probability densities in freestanding InAs dots3. A complementary technique, which probes theprobability density in k-space, makes use of magneto-tunneling spectroscopy.Self-assembled quantum dots (QDs) have been thor-oughly investigated in the last few years, using electronicand optoelectronic methods6-7. The high interest in these nanoscopic systems stems from their potential application inlaser devices or for quantum computing due to their control-lable and discrete spectrum of energy levels.Here we present a novel technique to map out the quasi-particle wave function for interacting electrons in self-assembled QDs, embedded in a field-effect transistor (FET)structure8-9. High-resolution maps of the wave functions areobtained using capacitance-voltage (CV) spectroscopy7-9 in variable magnetic fields.The samples contain InAs QDs embedded in a capacitor-like heterostructure between a Si-doped GaAs back contact and a surface gate. We have investigated two types of sam-ples, which differ slightly in the thickness d1 of the triangulartunneling barrier (see Fig. 1 (a)) that separates the dots from the back contact. The characteristic decay time of tunnelingelectrons10 depends roughly exponentially on the thicknessof the barrier, which is equal to d1 = 40 nm for sample type A and d1 = 42.5 nm for type B. For details of the layer struc-ture and growth procedure, see e.g. [9].For the CV spectroscopy, we apply a DC gate bias with an additional AC voltage (5 mV rms) of variable frequency fand measure the capacitive response signal. Fig. 1(a) shows the conduction band profile of our heterostructure for twodifferent DC voltages. With increasing bias, electronic dotstates in the quantum well can be shifted with regard to the chemical potential µbc in the back contact so that, in reso-nance, tunneling of electrons back and forth between the reservoir and the dots occurs, leading to an increase in themeasured capacitance. At sufficiently high frequencies, theAC modulation period will become shorter than the charging time, so that the capacitance maximum will be suppressed. It can be shown that the amplitude of the charging peak di-rectly reflects the tunneling probability10.For the wave function mapping, we follow the approachof Patanè et al.5 and apply a magnetic field B perpendicular to the tunneling direction z (see Fig. 1 (b)), at various angles in the x-y-plane.Due to the Lorentz force caused by the magnetic field, tunneling electrons from the back contact into the dots will acquire an additional momentum11heBdk1=∆. (1)Thus, the overlap of wave functions in the electron reser-voir (ϕbc(k–∆k)) and the dots (ϕdot(k)) can be altered by changing the in-plane field B. As the capacitive signal is proportional to the tunneling probability, which in turn is given by the overlap of the wave functions, we are able to obtain information on the shape of ϕdot(k).Using capacitance spectroscopy rather than measuring the current through resonant tunneling diodes5 has a number of advantages. First, we are measuring a large number of dots simultaneously, which gives us information on charac-teristic dot properties. Also, the large number of dots probed provides for a high signal-to-noise ratio12.Furthermore, the AC frequency f can be adjusted to ac-count for the fact that the tunneling current increases exponentially with increasing energy. Therefore, we can set f to optimize the wave function mapping. Finally, in our FET structures, it is possible to control the number of electrons N e in the dots by simply changing the DC gate voltage. Due to superimposed AC voltage, only the last electron tunnels in and out of the dots. This way, we probe the quasi-particle wave function13 of the last electron added to the dot, which gives information on interactions that govern the many-particle states in self-assembled dots.By varying the magnetic field amplitudes between 0 and 11 T and the field direction within the x-y-plane in 20 steps of 18°, we obtain three-dimensional plots of the tunneling probability in k-space.Fig. 1(c) shows a series of CV traces for sample B with a tunneling barrier of d1 = 42.5 nm at 4.2 K. The uppermost curves are typical low frequency traces9 (f = 35 Hz), show-ing two distinct peaks (s1, s2), related to the filling of the so-called s-shell of the QDs6-10,14, followed by four peaks14 of the p-shell (p1p2p3p4), which are not resolved here but coa-lesce into a broad shoulder. The lower CV traces (offset for clarity) are taken on the same sample at f = 12 kHz for vari-ous magnetic fields.At sufficiently high frequencies, all charging peaks can be reduced in amplitude by application of a magnetic field, with a full suppression to the background capacitance at 8 T (lowest curve). Care has to be taken when choosing an ap-propriate modulation frequency. For each charging peak we choose a frequency which is high enough to ensure that thepeak amplitude is given by the tunneling probability (rather than by the geometric parameters10) and at the same time low enough so that a good signal-to-noise ratio is obtained. We find that is this regime, the measured (normalized) prob-abilities are frequency independent.To map out the s-states, we have plotted in Fig. 2 the CV peak heights for s1 and s2 (sample A) as a function of the magnetic field. The top scale in the figure gives the corre-sponding momentum evaluated from Eq. (1). At the edges of the plots, the data agree quite well with the commonly used parabolic model5-7,13-15, however, we observe characteristic deviations at the center of the wave function (arrows). For small magnetic fields, tunneling can actually be increased, resulting in a center dip in the probability densities.A comparison between both s-states is of interest as it di-rectly shows the influence of the additional electron on the measured probability. Because of the repulsive electron-electron interaction, one would intuitively expect that the wave function should occupy a larger volume in real space when a second electron is added to the dot. Similarly, due to the higher energy for the doubly occupied s2 state, the corre-sponding wave function is expected to spread further into the confining potential. We observe, however, that the state s2 (FWHM: 7.6⋅108 m–1) is more extended in k-space, and therefore smaller in real space than the s1 state (FWHM: 5.5⋅108 m–1). One possible explanation could be the fact that the s2 state corresponds to a filled electronic shell and that – similarly as in atomic physics – configurations with com-pletely filled shells have smaller electronic radii than singly occupied orbitals. However, calculations using a parabolic confinement13 do not reproduce this behavior and a more detailed investigation is needed to clarify its origin.The charging peaks of the p-states are not as clearly sepa-rated as those of the s-states and can therefore not be mapped individually. We find, however, when a magnetic field is applied, that the p1 and p2 peaks show a distinctly different behavior from the p3 and p4 peaks (cf. Figure 1(c)). This reflects the fact that here, the electrons corresponding to p1 and p2 (p3 and p4) are in the same orbital state, respec-tively. We therefore evaluate the two lower (p1p2) and two higher (p3p4) states jointly in the following.Fig. 3 shows maps of the respective tunneling probabili-ties (sample B). In both cases, as expected for the p-states in x-y-representation, we observe a non-monotonic behavior with a minimum in the center and two maxima, which are in orthogonal directions for the two different pairs. However, unlike the single particle states in the harmonic oscillator model, the minima in the center do not fall to zero but still indicate finite tunneling probabilities for B = 0.A comparison of the plots for p1p2 and p3p4 shows, in analogy to the s-states, a wave function that extends further in k-space for N e = 5 – 6 (completely filled p-shell) than for N e = 3 – 4.The consecutive filling of the same spatial orbital for the two sequences p1p2 and p3p4, respectively, shows in a sur-prisingly clear way that the commonly assumed circular or square symmetry of the dots is lifted so that Hund’s rule16 can not be applied. In the contour plots in Fig. 3, this is demonstrated by the oval shape of the probability densities, clearly oriented along the 〈110〉 crystal axes. The lower states (p1p2) are always elongated along the [011] direction in real space. The lifting of degeneracy can either be attrib-uted to piezoelectric effects7,17-18 or to a slight elongation of the InAs island shape15. A piezoelectric potential is induced in the material by strain, which remains despite the relaxa-tion processes that take place during the growth procedure. FIG. 2. Tunneling probabilities for the first (s1) and second (s2) electron in InAs quantum dots (sample A) in k-space, where s2is offset for clarity. Filled squares indicate measured data for s1 and empty squares data for s2, the lines are Gaussian fits. The corre-sponding CV data was measured at 5.1 kHz. The inset shows the full rotational plots of the measured probability densities.FIG. 1. (a) Conduction band profile of the heterostructure for two different biases, (b) directions of the current and magnetic field, where x-y is the sample plane. (c) Low-temperature (T = 4.2 K) CV traces for sample B (d1= 42.5 nm) taken at low and high fre-quency. The curves show the influence of an in-plane magnetic field on the s-states (0 T, 3 T, 4 T, 5 T and 8 T, top to bottom) and on the p-states (0 T (dashed), 2 T, 5 T and 8 T).An elongation of the dot shape caused by anisotropic Indiffusion during growth has been proposed before15,19, but seems to be too small to be the only reason responsible for the noticeable effect here. Therefore, we expect an additional contribution from the piezoelectric potential, which has an anisotropic modulation17 and breaks the symmetry in the dot.Also, due to the high resolution of our plots, we can iden-tify a fine structure in both maps, which is more pronounced in the p1p2-states. In addition to the sharp maximum along the [011] direction, we observe a shoulder at higher k y-values (see arrows in Fig. 3(a)). This is a clear evidence for the complex electronic structure of the quasi-particle states.In conclusion, we have demonstrated a new capacitive technique to map out the wave functions in InAs quantum dots. As the occupation number in the dots can be controlled, our approach gives access to the addition spectra of interact-ing electrons into many-particle states. We find that the quasi-particle wave function decreases in size when elec-tronic shells are completed, in agreement with smaller atomic radii for filled shells in atomic physics.Furthermore, we find a lifting of the degeneracy along the 〈110〉-type crystal axes and a fine structure in the mag-neto-tunneling maps, which can so far not be explained.The authors would like to thank Alexander Govorov, Pe-ter Entel, Dietrich Wolf, Elisa Molinari and Massimo Ron-tani for valuable discussions and the latter also for making the data of Ref. [13] available to us. 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Fricke, A. Lorke, J. P. Kotthaus, G. Medeiros-Ribeiro, and P. M. Petroff, Europhys. Lett. 36, 197 (1996).16 S. Tarucha, D. G. Austing, and T. Honda, Phys. Rev. Lett. 77, 3613 (1996).17 J. H. Davies, Appl. Phys. Lett. 75, 4142 (1999).18 O. Stier, M. Grundmann, and D. Bimberg, Phys. Rev. B 59, 5688 (1999).19 S. Hameau, Y. Guldner, O. Verzelen, R. Ferreira, G. Bastard, J. Zeman,A. Lemaître and J. M. Gérard, Phys. Rev. Lett. 83, 4152 (1999).FIG. 3. (a) and (b) Surface plots of the quasi-particle wave function for sample B probed at a frequency of 12 kHz for the low-energy (p1p2) and high-energy p-states (p3p4). (c) and (d) Corresponding contour plots.。