Properties of Different RhB Solutions Used by Three Different Authors for Fluorescence-Based Temperature Measurements.
\\n\\n
IntechOpen Book Series will also publish a program of research-driven Thematic Edited Volumes that focus on specific areas and allow for a more in-depth overview of a particular subject.
\\n\\nIntechOpen Book Series will be launching regularly to offer our authors and editors exciting opportunities to publish their research Open Access. We will begin by relaunching some of our existing Book Series in this innovative book format, and will expand in 2022 into rapidly growing research fields that are driving and advancing society.
\\n\\nLaunching 2021
\\n\\nArtificial Intelligence, ISSN 2633-1403
\\n\\nVeterinary Medicine and Science, ISSN 2632-0517
\\n\\nBiochemistry, ISSN 2632-0983
\\n\\nBiomedical Engineering, ISSN 2631-5343
\\n\\nInfectious Diseases, ISSN 2631-6188
\\n\\nPhysiology (Coming Soon)
\\n\\nDentistry (Coming Soon)
\\n\\nWe invite you to explore our IntechOpen Book Series, find the right publishing program for you and reach your desired audience in record time.
\\n\\nNote: Edited in October 2021
\\n"}]',published:!0,mainMedia:{caption:"",originalUrl:"/media/original/132"}},components:[{type:"htmlEditorComponent",content:'With the desire to make book publishing more relevant for the digital age and offer innovative Open Access publishing options, we are thrilled to announce the launch of our new publishing format: IntechOpen Book Series.
\n\nDesigned to cover fast-moving research fields in rapidly expanding areas, our Book Series feature a Topic structure allowing us to present the most relevant sub-disciplines. Book Series are headed by Series Editors, and a team of Topic Editors supported by international Editorial Board members. Topics are always open for submissions, with an Annual Volume published each calendar year.
\n\nAfter a robust peer-review process, accepted works are published quickly, thanks to Online First, ensuring research is made available to the scientific community without delay.
\n\nOur innovative Book Series format brings you:
\n\nIntechOpen Book Series will also publish a program of research-driven Thematic Edited Volumes that focus on specific areas and allow for a more in-depth overview of a particular subject.
\n\nIntechOpen Book Series will be launching regularly to offer our authors and editors exciting opportunities to publish their research Open Access. We will begin by relaunching some of our existing Book Series in this innovative book format, and will expand in 2022 into rapidly growing research fields that are driving and advancing society.
\n\nLaunching 2021
\n\nArtificial Intelligence, ISSN 2633-1403
\n\nVeterinary Medicine and Science, ISSN 2632-0517
\n\nBiochemistry, ISSN 2632-0983
\n\nBiomedical Engineering, ISSN 2631-5343
\n\nInfectious Diseases, ISSN 2631-6188
\n\nPhysiology (Coming Soon)
\n\nDentistry (Coming Soon)
\n\nWe invite you to explore our IntechOpen Book Series, find the right publishing program for you and reach your desired audience in record time.
\n\nNote: Edited in October 2021
\n'}],latestNews:[{slug:"webinar-introduction-to-open-science-wednesday-18-may-1-pm-cest-20220518",title:"Webinar: Introduction to Open Science | Wednesday 18 May, 1 PM CEST"},{slug:"step-in-the-right-direction-intechopen-launches-a-portfolio-of-open-science-journals-20220414",title:"Step in the Right Direction: IntechOpen Launches a Portfolio of Open Science Journals"},{slug:"let-s-meet-at-london-book-fair-5-7-april-2022-olympia-london-20220321",title:"Let’s meet at London Book Fair, 5-7 April 2022, Olympia London"},{slug:"50-books-published-as-part-of-intechopen-and-knowledge-unlatched-ku-collaboration-20220316",title:"50 Books published as part of IntechOpen and Knowledge Unlatched (KU) Collaboration"},{slug:"intechopen-joins-the-united-nations-sustainable-development-goals-publishers-compact-20221702",title:"IntechOpen joins the United Nations Sustainable Development Goals Publishers Compact"},{slug:"intechopen-signs-exclusive-representation-agreement-with-lsr-libros-servicios-y-representaciones-s-a-de-c-v-20211123",title:"IntechOpen Signs Exclusive Representation Agreement with LSR Libros Servicios y Representaciones S.A. de C.V"},{slug:"intechopen-expands-partnership-with-research4life-20211110",title:"IntechOpen Expands Partnership with Research4Life"},{slug:"introducing-intechopen-book-series-a-new-publishing-format-for-oa-books-20210915",title:"Introducing IntechOpen Book Series - A New Publishing Format for OA Books"}]},book:{item:{type:"book",id:"6767",leadTitle:null,fullTitle:"New Trends in Electrical Vehicle Powertrains",title:"New Trends in Electrical Vehicle Powertrains",subtitle:null,reviewType:"peer-reviewed",abstract:"The electric vehicle and plug-in hybrid electric vehicle play a fundamental role in the forthcoming new paradigms of mobility and energy models. The electrification of the transport sector would lead to advantages in terms of energy efficiency and reduction of greenhouse gas emissions, but would also be a great opportunity for the introduction of renewable sources in the electricity sector. The chapters in this book show a diversity of current and new developments in the electrification of the transport sector seen from the electric vehicle point of view: first, the related technologies with design, control and supervision, second, the powertrain electric motor efficiency and reliability and, third, the deployment issues regarding renewable sources integration and charging facilities. This is precisely the purpose of this book, that is, to contribute to the literature about current research and development activities related to new trends in electric vehicle power trains.",isbn:"978-1-78985-022-2",printIsbn:"978-1-78985-021-5",pdfIsbn:"978-1-83881-698-8",doi:"10.5772/intechopen.72524",price:119,priceEur:129,priceUsd:155,slug:"new-trends-in-electrical-vehicle-powertrains",numberOfPages:234,isOpenForSubmission:!1,isInWos:null,isInBkci:!1,hash:"92949d7c2133b98bbddb02a9037c1dc7",bookSignature:"Luis Romeral Martínez and Miguel Delgado Prieto",publishedDate:"January 30th 2019",coverURL:"https://cdn.intechopen.com/books/images_new/6767.jpg",numberOfDownloads:18864,numberOfWosCitations:20,numberOfCrossrefCitations:11,numberOfCrossrefCitationsByBook:4,numberOfDimensionsCitations:27,numberOfDimensionsCitationsByBook:4,hasAltmetrics:1,numberOfTotalCitations:58,isAvailableForWebshopOrdering:!0,dateEndFirstStepPublish:"December 5th 2017",dateEndSecondStepPublish:"January 4th 2018",dateEndThirdStepPublish:"February 24th 2018",dateEndFourthStepPublish:"May 15th 2018",dateEndFifthStepPublish:"July 14th 2018",currentStepOfPublishingProcess:5,indexedIn:"1,2,3,4,5,6,7",editedByType:"Edited by",kuFlag:!1,featuredMarkup:null,editors:[{id:"86501",title:"Dr.",name:"Luis",middleName:null,surname:"Romeral Martinez",slug:"luis-romeral-martinez",fullName:"Luis Romeral Martinez",profilePictureURL:"https://mts.intechopen.com/storage/users/86501/images/system/86501.jpeg",biography:"Dr. Luis Romeral was born in Asturias, Spain, in 1960. He received his electrical engineering degree and the Ph.D degree from the Technical University of Catalonia (UPC) in 1985 and 1995, respectively. In 1988 he joined the Electronic Engineering Department of the UPC, where he is currently Associate Professor. His research interests include electric machines, power electronics converters and modulation strategies, variable-speed drive systems and fault detection algorithms. He has authored more than 250 peer reviewed scientific papers published in technical journals and conference proceedings. Over the last ten years, 10 Ph.D. dissertations have been completed under his supervision. He participates as a partner or responsible in European-Union funded projects, and research projects funded by Spanish agencies. He has also participated as engineer or project manager for research and development projects funded by local private companies, in the areas of control automation, industrial networking and supervision and data acquisition.",institutionString:"Technical University of Catalonia",position:null,outsideEditionCount:0,totalCites:0,totalAuthoredChapters:"1",totalChapterViews:"0",totalEditedBooks:"2",institution:null}],equalEditorOne:null,equalEditorTwo:null,equalEditorThree:null,coeditorOne:{id:"234568",title:"Dr.",name:"Miguel",middleName:null,surname:"Delgado Prieto",slug:"miguel-delgado-prieto",fullName:"Miguel Delgado Prieto",profilePictureURL:"https://mts.intechopen.com/storage/users/234568/images/system/234568.jpeg",biography:"Dr. M. Delgado-Prieto was born in Barcelona, Spain, in 1983. He received the M.S. and Ph.D. degrees in Electronics Engineering from the UPC, Barcelona, Spain, in 2007 and 2012, respectively. In 2008 he joined the MCIA Research Center of the UPC. In 2021 he joined the Automatic Control Department of the UPC as Assistant Professor. His activity includes research, technology transfer and project management on condition based monitoring and internet of things for the transport, industry and energy sectors, trough national and international cooperation with companies, research centers and universities. His research interests include condition monitoring, predictive maintenance, fault detection algorithms, machine learning, signal processing methods and embedded systems.",institutionString:"Universitat Politècnica de Catalunya",position:null,outsideEditionCount:0,totalCites:0,totalAuthoredChapters:"0",totalChapterViews:"0",totalEditedBooks:"0",institution:{name:"Universitat Politècnica de Catalunya",institutionURL:null,country:{name:"Spain"}}},coeditorTwo:null,coeditorThree:null,coeditorFour:null,coeditorFive:null,topics:[{id:"829",title:"Automobile Engineering",slug:"vehicle-engineering-automobile-engineering"}],chapters:[{id:"61412",title:"Model Based System Design for Electric Vehicle Conversion",doi:"10.5772/intechopen.77265",slug:"model-based-system-design-for-electric-vehicle-conversion",totalDownloads:3063,totalCrossrefCites:0,totalDimensionsCites:2,hasAltmetrics:1,abstract:"Development of electric vehicle (EV) conversion process can be implemented in a low-cost and time-saving manner, along with the design of actual components. Model-based system design is employed to systematically compute the power flow of the electric vehicle propulsion and dynamic load. Vehicle specification and driving cycles were the two main inputs for the simulation. As a result, the approach is capable of predicting various EV characteristics and design parameters, such as EV performance, driving range, torque speed characteristics, motor power, and battery power charge/discharge, which are the necessity for the design and sizing selection of the main EV components. Furthermore, drive-by-wire (DBW) ECU function can be employed by means of model-based design to improve drivability. For the current setup, the system components are consisted of actual ECU hardware, electric vehicle models, and control area network (CAN) communication. The EV component and system models are virtually simulated simultaneously in real time. Thus, the EV functionalities are verified corresponding to objective requirements. The current methodology can be employed as rapid design tool for ECU and software development. Same methodology can be illustrated to be used for EV tuning and reliability model test in the future.",signatures:"Ananchai Ukaew",downloadPdfUrl:"/chapter/pdf-download/61412",previewPdfUrl:"/chapter/pdf-preview/61412",authors:[{id:"239213",title:"Dr.",name:"Ananchai",surname:"Ukaew",slug:"ananchai-ukaew",fullName:"Ananchai Ukaew"}],corrections:null},{id:"61493",title:"Motion Dynamics Control of Electric Vehicles",doi:"10.5772/intechopen.77261",slug:"motion-dynamics-control-of-electric-vehicles",totalDownloads:1854,totalCrossrefCites:0,totalDimensionsCites:0,hasAltmetrics:0,abstract:"In this chapter, I will explain the dynamics of electric vehicle and the support systems of drivers in detail, considering both structure and the function of the vehicle. Furthermore, the reliability is discussed. In car development and design that I have, car dynamic control system, turn ability, comfort, and safety must all be considered simultaneously. The safety and the comfort for the driver which are connected with various road surfaces and as well as the speed depend on the physical performance of the vehicle. In this chapter, we will explain the dynamics of the vehicle and the support system of the driver in detail, considering both the structure and function of the vehicle. In the design and development of car dynamic control system, turn ability, comfort, and safety must all be considered simultaneously. The safeness and comfort during a drive on various road surfaces and speed depend on the performance of these basic abilities of the vehicle.",signatures:"Shinji Kajiwara",downloadPdfUrl:"/chapter/pdf-download/61493",previewPdfUrl:"/chapter/pdf-preview/61493",authors:[{id:"223635",title:"Prof.",name:"Shinji",surname:"Kajiwara",slug:"shinji-kajiwara",fullName:"Shinji Kajiwara"}],corrections:null},{id:"60174",title:"Adaptive Control for Estimating Insulation Resistance of High- Voltage Battery System in Electric Vehicles",doi:"10.5772/intechopen.75468",slug:"adaptive-control-for-estimating-insulation-resistance-of-high-voltage-battery-system-in-electric-veh",totalDownloads:1176,totalCrossrefCites:0,totalDimensionsCites:0,hasAltmetrics:0,abstract:"To ensure electrical safety and reliability in electric vehicles equipped with a high-voltage battery pack, an insulation monitoring circuit is indispensable to continuously monitor the insulation resistance during charging or driving. Existing methods such as injecting specific signals into the monitoring circuit and earth help to extract the resistance value from the voltage waveform. However, parasitic or stray capacitances in the monitoring circuit, which might introduce higher order dynamics into the waveform, are ignored. To avoid estimation error, the insulation resistance must be known in advance to carry out parameter calibration. In this chapter, one parasitic capacitance is applied in the circuit model and a new adaptive algorithm based on Lyapunov stability is employed to estimate the insulation resistance. This new online monitoring method and circuit are verified through simulation and experimentation, respectively. The results demonstrate that the proposed method can quickly react and track variations of insulation resistance on both positive and negative direct current (DC) lines.",signatures:"Yi-Hsien Chiang and Wu-Yang Sean",downloadPdfUrl:"/chapter/pdf-download/60174",previewPdfUrl:"/chapter/pdf-preview/60174",authors:[{id:"228433",title:"Prof.",name:"Wu-Yang",surname:"Sean",slug:"wu-yang-sean",fullName:"Wu-Yang Sean"},{id:"242445",title:"Dr.",name:"Yi-Hsien",surname:"Chiang",slug:"yi-hsien-chiang",fullName:"Yi-Hsien Chiang"}],corrections:null},{id:"62089",title:"Estimation Techniques for State of Charge in Battery Management Systems on Board of Hybrid Electric Vehicles Implemented in a Real-Time MATLAB/SIMULINK Environment",doi:"10.5772/intechopen.76230",slug:"estimation-techniques-for-state-of-charge-in-battery-management-systems-on-board-of-hybrid-electric-",totalDownloads:1835,totalCrossrefCites:1,totalDimensionsCites:1,hasAltmetrics:0,abstract:"The battery state-of-charge estimation is essential in automotive industry for a successful marketing of both electric and hybrid electric vehicles. Furthermore, the state-of-charge of a battery is a critical condition parameter for battery management system. In this research work we share from the experience accumulated in control systems applications field some preliminary results, especially in modeling and state estimation techniques, very useful for state-of-charge estimation of the rechargeable batteries with different chemistries. We investigate the design and the effectiveness of three nonlinear state-of-charge estimators implemented in a real-time MATLAB environment for a particular Li-Ion battery, such as an Unscented Kalman Filter, Particle filter, and a nonlinear observer. Finally, the target to be accomplished is to find the most suitable estimator in terms of performance accuracy and robustness.",signatures:"Roxana-Elena Tudoroiu, Mohammed Zaheeruddin, Sorin-Mihai\nRadu and Nicolae Tudoroiuv",downloadPdfUrl:"/chapter/pdf-download/62089",previewPdfUrl:"/chapter/pdf-preview/62089",authors:[{id:"239295",title:"Dr.Ing.",name:"Nicolae",surname:"Tudoroiu",slug:"nicolae-tudoroiu",fullName:"Nicolae Tudoroiu"},{id:"239610",title:"Dr.",name:"Elena-Roxana",surname:"Tudoroiu",slug:"elena-roxana-tudoroiu",fullName:"Elena-Roxana Tudoroiu"},{id:"239611",title:"Dr.",name:"Sorin-Mihai",surname:"Radu",slug:"sorin-mihai-radu",fullName:"Sorin-Mihai Radu"},{id:"243050",title:"Dr.",name:"Mohamed",surname:"Zaheeruddin",slug:"mohamed-zaheeruddin",fullName:"Mohamed Zaheeruddin"}],corrections:null},{id:"62507",title:"Worked Example of X-by-Wire Technology in Electric Vehicle: Braking and Steering",doi:"10.5772/intechopen.76852",slug:"worked-example-of-x-by-wire-technology-in-electric-vehicle-braking-and-steering",totalDownloads:1375,totalCrossrefCites:1,totalDimensionsCites:1,hasAltmetrics:0,abstract:"The chapter emphasizes on the worked example of braking system and steering system for electric vehicle. The x-by-wire technology is investigated and validated comprehensively. Brake-by-wire is considered a new brake technology that uses electronic devices and control system instead of conventional brake components to carry out braking function based on wire-transmitted information. However, the physical parameters associated with braking function cause nonlinear characteristics and variations in the braking dynamics, which eventually degrade stability and performance of the system. Therefore, this study presents the design of fuzzy-PID controller for brake-by-wire (BBW) to overcome these undesired effects and also to derive optimal brake force that assists to perform braking operation under distinct road conditions and distinct road types. Electric power-assisted steering (EPAS) system is a new power steering technology for vehicles especially for electric vehicles (EV). It has been applied to displace conventional hydraulic power-assisted steering (HPAS) system due to space efficiency, environmental compatibility, and engine performance. An EPAS system is a driver-assisting feedback system designed to boost the driver input torque to a desired output torque causing the steering action to be undertaken at much lower steering efforts.",signatures:"Ameer Sider and Mohd Khair Hassan",downloadPdfUrl:"/chapter/pdf-download/62507",previewPdfUrl:"/chapter/pdf-preview/62507",authors:[{id:"239688",title:"Associate Prof.",name:"Mohd Khair",surname:"Hassan",slug:"mohd-khair-hassan",fullName:"Mohd Khair Hassan"},{id:"249989",title:"Mr.",name:"Ameer",surname:"Seder",slug:"ameer-seder",fullName:"Ameer Seder"}],corrections:null},{id:"60860",title:"Reliable Design of PMaSynRM",doi:"10.5772/intechopen.76355",slug:"reliable-design-of-pmasynrm",totalDownloads:1511,totalCrossrefCites:1,totalDimensionsCites:1,hasAltmetrics:1,abstract:"Electric vehicles require highly reliable and resilient electric motors, due to the harsh operating conditions they must withstand. To this end, there is a current trend to design rare-earth-free machines. Traction electric motors must be optimized in terms of efficiency, torque density, power factor, constant power speed ratio, and cost. Although different technologies are available, permanent magnet assisted synchronous reluctance motors (PMa-SynRM) are promising candidates for such applications. Nowadays, the optimal design process of electrical motors is based on finite element method (FEM) simulations. However, it is very time consuming with a heavy computational burden process, so in order to speed up the optimization process, it is very appealing to have an accurate pre-design of the machine. In this chapter, the electromagnetic pre-design of a PMaSynRM is developed. In the proposed electromagnetic pre-design process, the geometry of the machine is calculated based on analytical equations that take into account the thermal, electrical, magnetic, and mechanical behavior of the machine to ensure a suitable and reliable design.",signatures:"Carlos López-Torres, Antoni Garcia-Espinosa and Jordi-Roger Riba",downloadPdfUrl:"/chapter/pdf-download/60860",previewPdfUrl:"/chapter/pdf-preview/60860",authors:[{id:"243929",title:"Dr.",name:"Antoni",surname:"Garcia Espinosa",slug:"antoni-garcia-espinosa",fullName:"Antoni Garcia Espinosa"},{id:"243931",title:"Ph.D. Student",name:"Carlos",surname:"Lopez-Torres",slug:"carlos-lopez-torres",fullName:"Carlos Lopez-Torres"},{id:"244461",title:"Dr.",name:"Jordi-Roger",surname:"Riba Ruiz",slug:"jordi-roger-riba-ruiz",fullName:"Jordi-Roger Riba Ruiz"}],corrections:null},{id:"59729",title:"Outer Rotor SRM Design for Electric Vehicle without Reducer via Speed-Up Evolutionary Algorithm",doi:"10.5772/intechopen.74451",slug:"outer-rotor-srm-design-for-electric-vehicle-without-reducer-via-speed-up-evolutionary-algorithm",totalDownloads:1416,totalCrossrefCites:1,totalDimensionsCites:2,hasAltmetrics:0,abstract:"Reducers utilized in automotive industry provide motor to run in most effective region and transmission output torque to increase. However, they cause mass and cost to increase and also efficiency to decrease due to mechanical losses. The aim of this study is to design a direct drive motor (outer rotor switched reluctance motor (OR-SRM)) without reducer resulting in enhanced efficiency for electric vehicle (EV). To estimate dimension and electrical parameters of OR-SRM, mathematical equations are originally derived from its geometry. Considering the constraints of package size and outer diameter, all the dimension parameters of the motor are optimized via multi-objective genetic algorithm (MOGA) to get the desired efficiency and torque. In order to validate the results in the proposed approach, OR-SRM is modeled by Maxwell 3D using optimized dimension parameters. In-wheel OR-SRM with 18/12 poles (30 kW) is manufactured to employ it in an EV. Theoretical results are compared to experimental results. It can be concluded that the results are satisfactory.",signatures:"Zeki Omaç, Mehmet Polat, Mustafa Kaya, Eyyüp Öksüztepe, Haluk\nEren, Merve Yıldırım and Hasan Kürüm",downloadPdfUrl:"/chapter/pdf-download/59729",previewPdfUrl:"/chapter/pdf-preview/59729",authors:[{id:"240554",title:"Dr.",name:"Haluk",surname:"Eren",slug:"haluk-eren",fullName:"Haluk Eren"},{id:"240604",title:"Dr.",name:"Eyyüp",surname:"Öksüztepe",slug:"eyyup-oksuztepe",fullName:"Eyyüp Öksüztepe"},{id:"240605",title:"Dr.",name:"Mehmet",surname:"Polat",slug:"mehmet-polat",fullName:"Mehmet Polat"},{id:"240606",title:"Dr.",name:"Mustafa",surname:"Kaya",slug:"mustafa-kaya",fullName:"Mustafa Kaya"},{id:"240607",title:"Dr.",name:"Zeki",surname:"Omaç",slug:"zeki-omac",fullName:"Zeki Omaç"},{id:"240608",title:"Dr.",name:"Hasan",surname:"Kürüm",slug:"hasan-kurum",fullName:"Hasan Kürüm"},{id:"240609",title:"Dr.",name:"Merve",surname:"Yıldırım",slug:"merve-yildirim",fullName:"Merve Yıldırım"}],corrections:null},{id:"61599",title:"Lightweight High-Efficiency Power Train Propulsion with Axial- Flux Machines for Electric or Hybrid Vehicles",doi:"10.5772/intechopen.77199",slug:"lightweight-high-efficiency-power-train-propulsion-with-axial-flux-machines-for-electric-or-hybrid-v",totalDownloads:1811,totalCrossrefCites:0,totalDimensionsCites:0,hasAltmetrics:1,abstract:"The aim of this chapter is to present a new type of powertrain with dimensions and low weight, for vehicles with reduced carbon emissions, which have an axial synchronous machine with one stator and two rotor, with static converter that is simple and inexpensive, a broadcast transmission system using an electric differential, with the control of the two rotors so that they can operate as motor/generator, at the same rotational direction or in opposite directions, at the same speed value, at slightly different speeds or at much different speeds by using an original dual vector control with operating on dual frequency. This is a major concern of hybrid and electric vehicle manufacturers. Expected results: a lighter power train with 20% and an increase in 5% of electric drive efficiency, low inertia rotor at high speed, a compact electric drive system with high torque and simple control, intelligent energy management system with a new vision of technological and innovation development, and equal importance of environment protection. The electrical machines for hybrid (HEV) or electric (EV) drives include a variety of different topologies. According to outcomes of literature survey, induction machines alongside synchronous machines take the major place in HEV or EV power trains.",signatures:"Sorin Ioan Deaconu, Vasile Horga, Marcel Topor, Fabrizio\nMarignetti, Lucian Nicolae Tutelea and Ilie Nuca",downloadPdfUrl:"/chapter/pdf-download/61599",previewPdfUrl:"/chapter/pdf-preview/61599",authors:[{id:"40500",title:"Dr.",name:"Vasile",surname:"Horga",slug:"vasile-horga",fullName:"Vasile Horga"},{id:"42568",title:"Dr.",name:"Fabrizio",surname:"Marignetti",slug:"fabrizio-marignetti",fullName:"Fabrizio Marignetti"},{id:"238578",title:"Associate Prof.",name:"Sorin Ioan",surname:"Deaconu",slug:"sorin-ioan-deaconu",fullName:"Sorin Ioan Deaconu"},{id:"238583",title:"Prof.",name:"Lucian Nicolae",surname:"Tutelea",slug:"lucian-nicolae-tutelea",fullName:"Lucian Nicolae Tutelea"},{id:"238585",title:"Dr.",name:"Marcel",surname:"Topor",slug:"marcel-topor",fullName:"Marcel Topor"},{id:"238586",title:"Dr.",name:"Ilie",surname:"Nuca",slug:"ilie-nuca",fullName:"Ilie Nuca"}],corrections:null},{id:"64809",title:"The Spatio-Temporal Analysis of the Use and Usability Problems of EV Workplace Charging Facilities",doi:"10.5772/intechopen.80481",slug:"the-spatio-temporal-analysis-of-the-use-and-usability-problems-of-ev-workplace-charging-facilities",totalDownloads:960,totalCrossrefCites:0,totalDimensionsCites:0,hasAltmetrics:0,abstract:"With the worldwide calls to meet greenhouse gas targets and policy objectives by 2030, finding an electric vehicle (EV) on the way to work every day has become less surprising. Adapting to owning an EV is challenging to all potential users. Current users tend to rely on domestic charging for a more certain and less hassle charging opportunity. The demand is shifting towards workplace charging (WPC) as a cheap and convenient solution due to the relatively long time the car is parked there. WPC fills a critical gap in EV charging infrastructure needs by extending electric miles and building range confidence. This chapter reports on the social practice of using one of the WPC facilities in the UK. It investigates the use and usability problems that are faced (n = 12) by EV users at workplace environment in one of the UK public sector employer.",signatures:"Eiman Elbanhawy",downloadPdfUrl:"/chapter/pdf-download/64809",previewPdfUrl:"/chapter/pdf-preview/64809",authors:[{id:"241494",title:"Dr.",name:"Eiman",surname:"Elbanhawy",slug:"eiman-elbanhawy",fullName:"Eiman Elbanhawy"}],corrections:null},{id:"60938",title:"Electric Vehicles Integrated with Renewable Energy Sources for Sustainable Mobility",doi:"10.5772/intechopen.76788",slug:"electric-vehicles-integrated-with-renewable-energy-sources-for-sustainable-mobility",totalDownloads:3864,totalCrossrefCites:7,totalDimensionsCites:20,hasAltmetrics:0,abstract:"Across the globe, governments have been tackling the concerning problem of air-polluting emissions by committing significant resources to improving air quality. Achieving the goal of air purification will require that both the private and public sectors invest in clean energy technology. It will also need a transition from conventional houses to smart houses and from conventional vehicles to electric vehicles (EVs). It will be necessary to integrate renewable energy sources (RESs) such as solar photovoltaics, wind energy systems and diverse varieties of bioenergies. In addition, there are opportunities for decarbonisation within the transportation sector itself. Paradoxically, it appears that the same transportation sector might also present an opportunity for a speedy decarbonisation. Statistics indicate that transportation is responsible for 14% of global greenhouse gas (GHG) emissions. However, there are numerous options for viable clean technology, including the plug-in electric vehicles (PEVs). There are indeed many technologies and strategies, which reduce transportation emissions such as public transportation, vehicle light weighing, start-stop trains, improved engine technology, fuel substitution and production improvement, hydrogen, power-to-gas, and natural gas heavy fleets. This work concentrates on EV adoption integrated with RES. Specifically, this chapter examines the feasibility of significantly reducing GHG emissions by integrating EVs with RESs for sustainable mobility.",signatures:"Michela Longo, Federica Foiadelli and Wahiba Yaïci",downloadPdfUrl:"/chapter/pdf-download/60938",previewPdfUrl:"/chapter/pdf-preview/60938",authors:[{id:"238927",title:"Prof.",name:"Michela",surname:"Longo",slug:"michela-longo",fullName:"Michela Longo"},{id:"240528",title:"Dr.",name:"Wahiba",surname:"Yaïci",slug:"wahiba-yaici",fullName:"Wahiba Yaïci"},{id:"240529",title:"Prof.",name:"Federica",surname:"Foiadelli",slug:"federica-foiadelli",fullName:"Federica Foiadelli"}],corrections:null}],productType:{id:"1",title:"Edited Volume",chapterContentType:"chapter",authoredCaption:"Edited by"},subseries:null,tags:null},relatedBooks:[{type:"book",id:"9428",title:"New Trends in the Use of Artificial Intelligence for the Industry 4.0",subtitle:null,isOpenForSubmission:!1,hash:"9e089eec484ce8e9eb32198c2d8b34ea",slug:"new-trends-in-the-use-of-artificial-intelligence-for-the-industry-4-0",bookSignature:"Luis Romeral Martínez, Roque A. 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In the last two decades, in the areas of chemical and biochemical sciences, there has been a great interest towards using microfluidic systems, which are popularly known as micro-total analysis systems (μ-TAS) (Manz et al., 2010) or lab-on-a-chip systems. These systems improve analytical performance and also facilitate incorporating various functions of distributed systems on a single-chip instead of having a separate device for each function (Reyes et al., 2002). Temperature control inside microfluidic cells is often required in a variety of on-chip applications for enhanced results, without significantly affecting the temperatures of other building blocks of the μ-TAS. This is a big challenge because the microfluidic devices on the chip need to be selectively heated.
Heat energy has been in use for stimulating (increasing) chemical and biochemical reactions (reaction rates), which otherwise proceed slowly under ambient conditions. Rapid, selective, and uniform heating of fluid volumes ranging from a few microliters to as low as a few nanoliters is vital for a wide range of microfluidic applications. For example, DNA amplification by polymerase chain reaction (PCR) is critically dependent on rapid and precise thermo-cycling of reagents at three different temperatures between 50 °C and 95 °C. Another important and related application, temperature induced cell lysing, necessitates fluid temperature in the vicinity of 94 °C. Other potential applications of heating in a microchip format include organic/inorganic chemical synthesis (Tu., 2011), the investigation of reaction kinetics, and biological studies, to name a few.
A number of conduction-based heating approaches have been reported for microfluidic systems that include embedded resistive heaters, peltier elements, or joule heating under electro-osmotic and pressure driven flow conditions. Generally speaking, these methods require physical contact or close proximity between a fluid and a heated surface to transfer heat from that surface to the fluid. In microfluidic devices, when the fluid volumes approach nanoliters, heating rates will be potentially limited by the added thermal mass of the substrates used for heat transfer, and not by the fluid volume. The transfer of heat in such manner can also result in heating of large, undesired substrate areas creating spatial limitations for integration of multiple analysis functions on a single substrate. Additionally, the implementation of these heating methods will be limited to high thermal diffusivity substrates, such as silicon and glass, to maximize heat transfer rates. However, such substrates due to their high cost and complexity of the fabrication process are unsuitable for use in disposable devices. Due to a number of inherent problems associated with contact-mediated temperature cycling, a number of research groups have focused on the development of non-contact heating approaches. These non-contact heating approaches include heating based on hot air cycling, heating based on IR light, laser-mediated heating, halogen lamp-based heating, induction heating, and heating based on microwave irradiation. Hot air based heating method utilizes rapidly switching air streams of the desired temperature and transfer of air onto either polypropylene tubes or glass capillaries. However, the control and application of hot air streams on micro-fabricated integrated systems may not be easily accomplished without an impact on other structures or reactions to be executed on the chip. An inexpensive tungsten lamp as an IR source for rapidly heating small volumes of solution in a microchip format can potentially limit the heating efficiency when applied to microchips with smaller cross-section because the tungsten lamp is a non-coherent and non-focused light source leading to a relatively large focus projection. Other light based heating methods have been demonstrated for microfluidic heating, but such systems, generally speaking, require lenses and filters to eliminate wavelengths that could interfere with the reaction, and accurate positioning of the reaction mixture at the appropriate focal distance from the lamp, which further complicates their implementation.
Microwave dielectric heating is a candidate to address these issues. Most chemical and biochemical species are mainly comprised of water or solvated in water. Water is a very good absorber of microwave energy in the frequency range 0.3 GHz – 300 GHz.Due to this reason, microwave dielectric heating has been exploited for over five decades for heating and cooking fluids and food items containing water molecules (Brodie., 2011).It is also a very good candidate for implementing the heating function in chemical and biochemical reactions as well.
Advantages of microwave dielectric heating include its preferential heating capability and non-contact delivery of energy. The first advantage stems from the fact that the microwave energy can be directly delivered to the microfluid sample with little or no absorption from the substrate material (glass, PDMS). The latter advantage facilitates not only the faster heating rates but also the faster cooling rates. These characteristics of microwave dielectric heating allow the application of heat-pulse approaching a delta function, because the heating stops at the moment the microwave power is turned off. This aspect of microwave heating has been used by (Fermer et al., 2003) and (Orrling et al., 2004) for high-speed polymerase chain reactions. The mechanisms of chemical reactions assisted by microwave heating have been found to conform close to theory yielding much more reliable end-products (Zhang et al., 2003; Whittaker et al., 2002; Gedye et al., 1998; Langa et al., 1997). The chemical reactions assisted by the microwave heating have also been performed at much lower temperatures compared to the conventional heating methods (Bengtson et al., 2002; Fermer et al., 2003). Localized microwave heating of fluids has also been demonstrated in the systems having silicon field-effect-transistors in the vicinity of microfluids (Elibol et al., 2008; Elibol et al., 2009).
Enhanced thermo-cycling rates and reduced reaction times compared to conventional techniques can be achieved because of the inertialess nature of microwave heating. Microwave-mediated thermocycling has been demonstrated for DNA amplification application (Kempitiya et al., 2009; Marchiarullo et al., 2007; Sklavounos et al., 2006). Heating can also be made spatially selective by confining the electromagnetic fields to specific regions of the microfluidic network. Further, the dielectric properties of the fluid can also be exploited to deliver heat using signal frequency as a control parameter in addition to the power.
Microwave heating is also very attractive than other alternatives for obtaining spatial temporal temperature gradients for a variety of on-chip applications, including investigation of thermophoresis (Duhr et al., 2006), control and measurement of enzymatic activity (Arata et al., 2005; Mao et al., 2002; Tanaka et al., 2000), investigation of the thermodynamics (Baaskeet al., 2007; Mao et al., 2002), chemical separation (Buch et al., 2004; Huang et al., 2002; Ross et al., 2002; Zhang et al., 2007), and of the kinetics characterizing molecular associations (Braun et al., 2003; Dodge et al., 2004). Most techniques for generating on-chip temperature gradients integrate Joule heating elements to conduct heat into microchannels/microchambers (Arata et al., 2005; Buch et al., 2004, Selva et al., 2009). However, temporal control is limited by the heat capacity of the microfluidic device and thermal coupling of the device to the heating elements. It is easy to locally and rapidly generate temperature gradients within microchannels using the pattern of the microwave electric field intensity of a standing wave. The temperature distribution in the channel fluid is proportional to the time average of the square of the microwave electric field, which contains a sinusoidal component in the presence of a standing wave in the transmission line used to couple microwaves to the fluid in the microchannel. Using microwaves, a nonlinear sinusoidally shaped gradient along a channel of several millimeter length with aquasilinear temperature gradient can be achieved within a second (Shah et al., 2010). The electric field distribution can also be controlled via the operating frequency and input power, which provides flexibility in changing the temperature profile for different specimens, reactions or applications.
The water molecule has a permanent dipole (the central oxygen atom is electronegative compared to the hydrogen atoms, which are covalently bonded to the oxygen atom) and tends to align itself with an applied electric field. The resistance experienced by the water dipole molecule in aligning itself with the applied electric field is directly related to the intermolecular forces (hydrogen bonds formed by the oxygen atom of one water molecule with the hydrogen atoms of other water molecules) it encounters. Under an influence of sinusoidal applied electric field at a microwave frequency, the ensemble of water dipole molecules experience a rotational torque, in orienting themselves with the electric filed. The rotation caused by the applied field is constantly interrupted by collisions with neighbors. This process results in hydrogen bond breakage and the energy associated with the hydrogen bonds gets translated into the kinetic energy of the rotating dipoles. The higher the angular velocity of a rotating molecule, the higher the angular momentum, and consequently the higher is the kinetic energy. Thus, intermolecular collisions lead to friction, which causes dielectric heating. Dielectric heating is quantified by the imaginary part (ε\'\') of the dielectric constant. The value of ε\'\' (also called as the dielectric loss factor) depends on the frequency. As the frequency increases from the MHz range into the GHz range, the rotational torque exerted by the electric field increases; consequently, the angular velocity of the rotating dipoles increases, resulting in an increase in the value of ε\'\'.
The orientation of the molecular dipoles in response to the applied electric field results in the displacement of the charges, which generates displacement current according to the Maxwell-Ampere law. Dielectric heating is the result of interaction between the displacement current and the applied electric field. At low frequencies (MHz range) the molecular dipoles are able to follow the changes in polarity of the applied electric field (E). Thus, even though a displacement current (I) is generated, it is 90˚ out of phase with the applied electric field, resulting in a E × I = E・I・cos(90˚) = 0. Thus, no dielectric heating occurs at such frequencies. At frequencies ≥ 0.5 GHz, the molecular dipoles cannot keep pace with the rapidly changing polarity of the applied electric field, and hence the displacement current acquires a component, I・sinδ, in phase with the applied electric field, where δ is the phase lag between the applied electric field and molecular dipole orientation. This results in a E × I = E・I・cos(90˚- δ) ≠ 0, and consequently dielectric heating. At very high frequencies (≥ 50 GHz), the field changes too quickly for the molecular dipoles to orient significantly, hence, the displacement current component in phase with the applied electric field vanishes. Consequently, the extent of dielectric heating decreases at high frequencies.
The absorption depth of microwave power for liquid water in the 2 – 25 GHz region is few to several tens of centimeters (Jackson et al., 1975). Since the microchannels are typically 5 – 10 μm in depth, the electric field intensity is more or less constant throughout the microchannel.
The microwave power absorbed per unit volume in a dielectric material is given by:
where
is the dielectric conductivity of the material, fis the frequency in Hz,εois the permittivity of free space, ε\'\'is the imaginary part of the complex permittivity of the material (which depends on the frequency and temperature), and E is the electric field strength in V/m within the material. The ε\'\' is given by:
where, τ is the relaxation time, ω = 2πf is the angular frequency, εsis the static field permittivity, and ε∞ is the optical domain permittivity at frequencies much greater than the relaxation frequency (1/τ). The ε\'\' value first increases with increasing frequency reaching a peak value, before it starts decreasing with a further increase in frequency.
Experimental values for the permittivity and total loss factor as a function of frequency for aqueous KCl solutions of differing ionic concentrations (adapted from
The ions dissolved in water influence the rotational ability of the water molecules that are in close proximity to them. Under an external field, the mobile ions collide with the nearby water molecules transferring their kinetic energy to the water molecules, which is given out as heat. The ε\'\' value, and consequently the dielectric conductivity, increase with increasing ionic strength at low frequencies, but interestingly, as shown in Figure 1, it becomes relatively independent of ion concentration of solution over a small region of microwave frequencies. Therefore, such solutions can be heated with microwaves of this frequency regime independently of their ionic strength. This characteristic of microwave dielectric heating is particularly advantageous when the salt concentration of the solution is not a known
The water temperature also affects the microwave dielectric heating mechanism. With an increase in the water temperature, the strength and the extent of the hydrogen bonding network in water decreases, because more hydrogen bonds are already broken at a high temperature. This lowers the ε\'\' value and consequently a decrease in dielectric heating. It means the water becomes a poorer absorber of microwave power with increasing temperature, shifting the ε\'\' (or σ or Pv) versus frequency curve to higher frequencies. This can be an advantage when a steady temperature needs to be maintained.
The power density in a dielectric material upon exposure to alternating electromagnetic field is given by (Woolley et al., 1996)
where
where
where
The use of microwave heating has been demonstrated for a variety of applications including drug discovery, isolation of DNA, and heating of biological cells. Macro-scale microwave applicators were commonly utilized for the delivery of microwave power to sample contained in the plastic reaction tubes.
For microwave heating using a macroscale X-band rectangular waveguide, a slot is machined into one of the walls of the waveguide to allow the introduction of a microfluidic device, as shown in Figure 2. The position of the slot is chosen such that the microchip is placed perpendicular to the direction of the field propagation to maximize coupling of microwave power to fluid. The fluidic channel is micromachined into PMMA substrate using a milling machine. The channel enclosure is accomplished via thermal lamination technique with PP film. A traveling wave tube amplifier, capable of amplifying the input power up to 30 W over the 8 GHz to 18 GHz frequency range, coupled to a microwave signal generator is used to provide the desired microwave power; and a thermocouple inserted into the PMMA substrate is used to measure the fluid temperature. Further details of the system are given elsewhere (Shah, 2007b).
Thermo-cycling of de-ionized water between 60 °C and 95 °C is accomplished by this system, as shown in Figure 3.As mentioned earlier, DNA amplification by PCR relies on temperature cycling of thereaction mixture through three different temperatures between 50 °C and 95 °C. It means this system is suitable for DNA amplification by PCR. When a 20 W microwave power was applied the average heating rate of this system can be as high as 6 °C/s and the cooling rate 2.2 °C/s for a fluid volume of about 70 μL.
These values are better than what was accomplished (Figure 4) using a conventional metal block-based thermocycler whose heating and cooling rates are less than 1.7 °C/s. The results of Figure 3 confirm that microwave heating is a viable alternative for on-chip microfluidic systems, and that it can be used to obtain superior thermocycling rates compared to those obtained with conventional macroscalethermocyclers.
A schematic of an x-band rectangular waveguide heating system.
On-chip thermocycling of de-ionized water obtained using rectangular waveguide heating system.
Thermocycling of de-ionized water using macroscale conventional thermocycler. The PCR tubes were used to hold 25μL of fluid. The average heating rate for this system was 1.69 °C/s and the cooling rate was 1.36 °C/s.
In recent years the interest in microwave heating lie in integrating miniaturized microwave heating elements, in the form of transmission lines, with microfluidic channels for on-chip heating applications. In one such case, microwave power can be delivered to an elastomeric microfluidic channel via an integrated thin-film coplanar waveguide (CPW) two-conductor transmission line. The rest of the chapter focuses on the work our group has done on this topic in the past 10 years.
A schematic of a prototype coplanar waveguide (CPW) coupled with the microfluidic channel is shown in Figure 5. Typical dimensions are given in Figure 6. In this system a defined poly(dimethylsiloxane) (PDMS) microfluidic channel is aligned in the gap between the signal plane and one of the ground planes. The reason for choosing the CPW for delivering the microwave power to the microfluidic channel is that it can be easily formed on a substrate using a lift-off lithography process and its planar nature allows for easy integration with the microfluidic channels. The planar geometry also allows fabrication of an array of these devices on a common substrate with high yield, which later can be separated into individual devices.
The dimensions of the center conductor, the gap between the center conductor and the ground plane, the thickness and effective dielectric constant of the substrate determine the characteristic impedance (ZO) and effective dielectric constant of the line. Since, the CPW is a two-conductor transmission line with different dielectrics above and below the device plane, it supports a quasi-TEM mode as well as surface wave modes (Riaziat et al., 1990). The surface wave modes lead to energy transfer from the guided wave into the substrate leading to the attenuation of the guided wave. The CPW design solution is optimized to avoid all potential problems associated with the surface waves in choosing the substrate thickness less than the dielectric substrate wavelength, λd (Riaziat et al., 1990). For the design features shown in Figure 6, the substrate thickness is one-sixth of the λdvalue. The conductor loss in CPW is inversely proportional to the skin depth and metallization thickness. This leads to increased conductor attenuation with increasing microwave frequency and decreasing conductor thickness, however, the effect of conductor thickness on the conductor attenuation is not as dramatic as that of frequency. For a glass substrate, the dielectric attenuation (Gupta et al., 1996) is very insignificant compared to the conductor attenuation and can be ignored.
Schematic of coplanar waveguide (in orange) coupled with the microchannel structure (in pink)
Schematic of a cross-section of a coplanar waveguide (CPW) transmission line integrated with a poly(dimethylsiloxane) (PDMS) microchannel for microwave dielectric heating of fluids. The CPW conductors are 1.5 cm long; the signal conductor is 140 μm wide and it is separated by a 25 μm gap on either side from 300 μm wide ground conductors. The microchannel consists of a trapezoidal cross section defined by a silicon template and it is 7 μm deep, 25 μm wide at the bottom, and 3.62 mm long.
The CPW conductors are formed of Cr/Au on the substrate using standard lift-off lithography metallization process. Thickness of the CPW conductors is increased by electroplating of Au. A trapezoidal cross-section PDMS microfluidic channel is defined by using a silicon template. The PDMS is poured into the silicon master and cured for 4 hours at 65 ˚C for this purpose. The PDMS structure is then detached from the silicon master and holes are punched into the PDMS structure for creating fluid inlet and outlet for the channel. The PDMS microchannel is then carefully aligned and attached by contact adhesion in the lateral direction over the gap between the signal-ground metal lines of the CPW. For maximum electric field coupling, the width of the PDMS microchannel is made equal to the CPW signal-ground metal spacing. According to computer simulations about 50% of the electric field is contained within 10 microns from the CPW surface. Hence, the depth of the microchannel should be designed accordingly to couple as much of the electric field as possible to the microfluid in the channel.
Microwave power is applied at the input port of the CPW using a signal generator. The frequency of the microwaves can be varied for optimum coupling of the microwave power to the microfluid. S-parameters of the system are measured for empty channel case and also for liquids of varying ionic concentrations. The fluid temperature is obtained by measuring the temperature dependent fluorescence intensity of a dilute fluorophore dye added to the fluid and comparing it to the calibrated fluorescence intensity at a known temperature. Rhodamyne B is used as the dye solution for this purpose.
Figure 7shows a cross-sectional schematic and a picture of the microwave-heated microfluidic device for generating temperature gradients. The devices are fabricated using an adhesive copper tape oncyclic olefin copolymer (COC) using photolithographic procedures. A CNC milling machine is used to cut the substrate material to precise chip dimensions and to carve out the microchannel and thefluidic access ports. For the device in Figure 7 the microchannel is 340
a) A picture of the integrated microfluidic device for generating microwave-induced temperature gradients. (b) A cross-sectional view of the microwave heating device.
The method described here for fabricating conductors is easily transferable to other microfluidic substrates such as glass and PDMS. Furthermore, the one-step method for conductor fabrication obviates the need for electroplating, which is typically required following thin-film deposition to achieve sufficient conductor thickness. This method also provides easy bonding of the top and bottom cover plates to create enclosed channel structures, which has proven challenging for thermoplastic materials (Shah et al., 2006). In contrast to previously published reports (Shah et al., 2007a; Booth et al., 2006; Facer et al., 2001), the transmission line structure isolates the fluid from the metal conductors making these devices suitable for a variety of biochemical applications in which reagent contamination due to electrolysis or corrosion is undesirable.
The temperature-sensitive nature of molecular fluorescence is suitable for measurement of temperature in small volume fluids like in microfluidic channels ( Lou et al., 1999; Gallery et al., 1994; Sakakibara et al., 1993; Ali et al., 1990; Kubin et al., 1982). The temperature measurement is based on measuring fluorescence intensity ratios. The fluorescence intensity is typically measured at a known reference temperature, which is later used to normalize the intensity measured after heating the medium to an unknown temperature. The temperature is extracted by substituting the normalized intensity into a calibration curve. For lab-on-a-chip application,the use of dilute solutions of a temperature-sensitive fluorescent dye, particularly Rhodamine B (RhB), has become very popular for optical measurement of temperature distributions. The RhB is a water-soluble fluorescent compound with an absorption peak at 554 nm, an emission peak at 576 nm, and a temperature dependent fluorescence quantum yield (Ferguson et al., 1973). In addition to high temperature sensitivity, its other properties such as negligible pressure sensitivity and nominal pH-independent absorption (above a pH value of 6) are attractive for measuring temperatures in microfluidic channels with high spatial and temporal resolution (Ross et al., 2001). The RhB solution has been employed: to examine in-channel temperature and flow profiles at a T-shaped microchannel intersection during electrokinetic pumping (Erickson et al., 2003) and to characterize the temperature field resulting from resistive microheaters embedded in a poly(dimethylsiloxane) (PDMS) microchip (Fu et al., 2006). Even though the RhB has been primarily used for temperature measurement in aqueous environment, the absorbed RhB dye molecules in a PDMS thin film can be used for whole chip temperature measurement (Samy et al., 2008). The calibration equations used for computing temperature using fluorescent dyes relate the fluorescence intensity at an unknown temperature to the intensity at only one particular reference temperature. Such relations are not directly usable to applications requiring a different reference or initial temperature. The existing single-dye calibration equations have been generalized for extending their use to fluorescence intensity data normalized to reference temperatures other than those for which the original calibration equations were derived (Shah et al., 2009). Two methods have been described in detail: one is approximate, while the other, based on solution of a cubic equation, is an accurate mathematical treatment that does not incur errors beyond those already inherent in the calibration equations.
Let
Ross et al. | 0.1 | 20 | 9.4 | 132 | -250 | 220 | -79 | 23 | 22 |
Fu et al. | 0.05 | 25 | 8.5 | 149.15 | -317.84 | 323.41 | -131.84 | 22.88 | 23.5 |
Samy et al. | 1.0,5.0 | none | N/A | 141.53 | -250.25 | 228.02 | -96.904 | 22.39 | 23 |
Properties of Different RhB Solutions Used by Three Different Authors for Fluorescence-Based Temperature Measurements.
The fluorescence intensity acquired from an image captured at an elevated temperature,
to fit the measured IRT(T) for different values of T.
Table 1 includes the values of
Comparison of the relative fluorescence-intensity versus temperature calibrations published by
The calibration curves from all three authors are compared in Figure 8. The general trend of all three curves is similar. The difference between the curve of Samy et al., 2008 and the other two authors can be explained by the different physical medium and local environment used in the measurements.
Measurement of fluorescence intensity at a reference temperature in the vicinity of 23°C, for normalization purposes, is not always possible. For example, in applications requiring rapid temperature cycling of fluidic solutions the cycling temperatures of interest might be significantly different from 23 °C. In these situations, it is useful to calculate the fluorescence intensity ratio at a convenient reference temperature,
While it might appear plausible to use
With a different approach, it was possible to eliminate all additional error except that inherent to the calibration equations themselves. For this approach, the normalized fluorescence intensity is generalized by rewriting it as
where
with the values of
and
When
Experiments were performed to evaluate the performance of the CPW devices for heating in the microchannel environment. The device is characterized for its frequency response in order to obtain absorption ratios with empty and fluid-filled microchannels. The fluid temperature is measured at various microwave frequencies. The results obtained from the first experiment are used to derive a power absorption model to find the distribution of the incident microwave power in different absorbing structures of the device.
The CPW device frequency response is characterized by scattering (S) parameter measurements. The S-parameters relate the forward and reflected traveling waves in a transmission medium and can be used to understand the power flow as a function of frequency. The S-parameters are used in conjunction with the conservation of energy to model absorption of microwave power and to predict the fluid temperature based on the absorbed power. The predicted temperature is then fitted to the measured temperature to determine heating efficiency. The experiments for the results presented below were performed with deionized (DI) H2O and with fluids of two different salt concentrations: 0.9% NaCl solution and 3.5% NaCl solution.
The amplitude of the reflection coefficients (S11) and transmission coefficients (S21) from 0.3 GHz to 40 GHz for the device with an empty channel as well as for the fluid-filled channels are shown in Figure 9(a) and\n\t\t\t\t\t\tFigure 9(b), respectively. In comparison with the empty channel device, S11 is reduced for the device with fluid-filled channel and it approaches that of an empty channel for frequencies above 10.5 GHz. The decrease in S11 of the fluid-filled devices below 10.5 GHz which indicate good impedance matching conditions are apparently fortuitous. The S11 is also found to be almost independent of the ionic concentration of the fluid. The localized peak and trough features observed in the S11 are likely interference effects due to reflections at the probe-CPW interfaces and the CPW/air-CPW/fluid interfaces (Facer et al., 2001). The S21, as seen from Figure 9(b), decreases with
A) Measured reflection coefficients ( |S11| )of the device. (B) Measured transmission coefficients ( |S21| )of the device. (■) Empty microchannel, (●) microchannel filled with deionized H2O, (▲) microchannel filled with 0.9 % NaCl, (♦) microchannel filled with 3.5% NaCl.
increasing frequency for the devices with both the empty and fluid-filled channels. It is believed that the apparent low transmission coefficient of the empty-channel device is likely due to the smaller than optimum thickness of the CPW conductors (0.5
Figure 10 shows percent absorption ratios (the fraction of the incident power absorbed by the device) as a function of frequency for the devices with empty and fluidfilledmicrochannels. The absorption ratio,
The percent absorption ratios (the fraction of the incident microwave power absorbed by the device) as a function of frequency. The absorption ratio, A, was calculated from the measured transmission and reflection coefficients using
It seems from Figure 10 that the simplest approximation to the fraction of the incident microwave power absorbed in the fluid is the difference between the power absorbed by the full-channel and empty-channel devices (for the case of water-filled device,
Top view of a CPW integrated with an elastometricmicrochannel consisting of three regions, center region with the microchannel and the two end regions without the microchannel.
microchannel and two end regions that have no microchannel over them. The lengths of each of the three regions are defined by the center region, Z2, 0.36 cm long and two end regions, Z1 and Z3, each 0.57 cm long. The reflectance at the interface between the regions is assumed to be negligible, and the transmission coefficient,
The derivation of this equation is based on exponential attenuation of microwave power in the direction of propagation where the rate of decay with distance is described by the attenuation constant,
Finally, the absorption ratios of the water,
The distribution of the incident microwave power in different absorbing structures of deionized H2O filled device as obtained from the alpha absorption model.
Eqns 12 through 15 are first order approximations. For impedance matched conditions, the equations show that
The points (■) in Figure 13 show the fluid (aqueous solution of Rhodamine B) temperature measured at various microwave frequencies. The applied power was kept constant at 10 mW. The temperature was measured ~ 250 ms after turning on the microwave power, which was approximated to be within 5% of quasi-thermal equilibrium. The error bars indicate the pooled standard deviation over all measurements for two instances at each frequency added with the estimated standard deviation (0.5 °C) of the room temperature (22.5 °C). The observed temperature rise was 0.88 °C/mW at 12 GHz and 0.95 °C/mW at 15 GHz.
The measured temperature (■) of an aqueous solution of 0.2 mmol/L Rhodamine B in a 19 mmol/L carbonate buffer as a function of frequency. The solid line indicates predicted temperature calculated from the alpha absorption model, and the dashed line was calculated by employing the power difference model.
The temperature can also be calculated from the energy absorbed in the water during the heating period
Where ρ and
The choice of COC and Cu tape for the microfluidic cell (Figure 7) offers several advantages for producing ntegrated microfluidic devices for microwave heating. The high glass transition temperature of COC (
An electromagnetic simulation of a geometrical structure similar to that shown in Figure7(a) was performed using Sonnet Software with nominal properties for copper, acrylic, COC and water. The design parameters were varied to optimize microwave power absorption in the fluid since absorption governs the maximum attainable temperature. A trade-off relation was found to exist between the power absorbed in the fluid and the ratio of the channel height to the total substrate thickness (the sum of cover plates and COC thickness). A smaller channel height to substrate thickness ratio reduced the absorbed power for a given fluid volume and incident microwave power. The coupling of the microwave power from the amplifier (less than, but approximately equal to 1W) to the transmission line and the microchannel was characterized theoretically and experimentally by measuring the reflection coefficient (
Figure 14 shows the simulated and measured absorption ratios for the empty-channel and water filled device. Close agreement is found in both the amplitude and shape for the full-channel device, but only in shape for the empty-channel device with the correlation coefficient of 0.98 for the empty-channel device and 0.96 for the water filled device. The amplitude deviation in the experimental absorption ratio for the empty-channel device can be attributed to imperfections in the as-fabricated conductor. However, this difference is much smaller for the water-filled device apparently because fluid absorption dominates the absorptive process. The
Comparison between simulated and measured absorption ratios, the fraction of the incident microwave power absorbed by the device, as a function of frequency. The simulated and measured responses are compared for the empty channel as well as the water-filled device. The curves are constructed from S-parameter data according to A = 1 - |S11| - |S21|, where S11 is the reflection coefficient and S21 is the transmission coefficient. The upper dotted line is simulated full channel response, the upper solid line is measured full channel response, the lower solid line is measured empty channel response, and the lower dotted line is the simulated empty channel response.
device. The absorbed power increases with increasing frequency, and the peaks in the absorbed power exist at a variety of frequencies (Figure 14). However, the amplitude of the absorbed power at the peaks for frequencies lower than 12 GHz is significantly smaller than that at 12 GHz and above. Here, the resultsof temperature measurements at the lowest (12 GHz) and highest (19 GHz) frequencies that gave relatively large peaks in the absorption ratio data are shown.
Figure 15 shows the experimental temperature profile for the excitation frequency of 19 GHz. The curve in Figure 15 was constructed by using the calibration curve of Rhodamine B dye to convert the fluorescence intensity into temperature. A nonlinearly modulated profile extending along the length of the microchannelwas observed. The temperatures measured at different positions was compared with the model of temperature gradient generation by performing nonlinear least-squares fitting of equation 6 to the measured data points using Origin software (solid line in Figure 15) and a good agreement (
12 GHz | 19 GHz | |||
Value | SD | Value | SD | |
6.986 | 0.051 | 6.31 | 0.024 | |
0.501 | 0.041 | -0.281 | 0.017 | |
β (deg mm-1) | 29.11 | 0 | 46.35 | 0.974 |
θp (deg) | 264.8 | 3.25 | 154.1 | 7.071 |
α (mm-1) | 0.015 | 0.002 | 0.01 | 0.001 |
Chi-square | 1.193 | - | 0.257 | - |
0.975 | - | 0.981 | - |
Results from nonlinear least-squares fitting of the temperature gradient model (equation 6) to the measured data points shown in Figures 15 and 16 for one device. A standard error of zero indicates that this value was fixed during the fit.
12 GHz | 19 GHz | |||
Mean | Average SD | Mean | Average SD | |
6.912 | 0.049 | 6.427 | 0.035 | |
0.502 | 0.04 | 0.092 | 0.025 | |
β (deg mm-1) | 29.106 | 0.04 | 46.123 | 1.833 |
θp (deg) | 259.4 | 3.229 | 193.6 | 14.22 |
α (mm-1) | 0.011 | 0.002 | 0.012 | 0.002 |
Chi-square | 1.142 | - | 0.712 | - |
0.971 | - | 0.923 | - |
The average and standard deviations of the fitting parameters extracted from nonlinear least-squares fitting of measured temperature gradient data to the theoretical model shown in equation (6). A standard deviation of zero indicates that this valuewas fixed during the fit as described in the text.
The measured temperature versus distance along the microchannel of an aqueous solution of 0.2 mmol L-1Rhodamine B in a 19 mmol L-1 carbonate buffer at the microwave excitation frequency of 19 GHz. The solid line represents a theoretical temperature fit to the measured data points shown by squares. The measurement frequency was selected based on a local maximum in
The measured temperature of an aqueous solution of 0.2 mmol L-1Rhodamine B in a 19 mmol L-1 carbonate buffer as a function of position along the microchannel at the microwave excitation frequency of 12 GHz. The solid line represents a theoretical temperature fit to the data points shown by squares. The measurement frequency was selected based on a local minimum in S11 (not shown here) and a local maximum in
For a given geometrical structure, the nonlinear temperature profile (Figure 15) can be altered by changing the frequency of the microwave signal. This is demonstrated in Figure 16, which shows the spatial temperature profile obtained for 12 GHz excitation frequency. Here, a nonlinear profile representing a sinusoidal wave extending along the length of the microchannel was observed. The data also resulted in a quasilinear temperature gradient with a slope of 7.3 °C mm−1 along a 2 mm distance. Linear temperature gradients with comparable slopes have been used for DNA mutation detection (Bienvenue et al., 2006), phase transition measurements in phospholipid membranes (Saiki et al., 1986), single-nucleotide polymorphism (SNP) analysis (Baker., 1995) and continuous-flow thermal gradient PCR (Liu et al., 2007). As before, nonlinear least-squares fitting of the theoretical model (solid line in Figure16) to the experimental data shows good agreement (
It should be possible to prevent the absorption of Rhodamine B dye on the microchannel surface by modifying those surfaces with appropriate surface treatments as is typically done for analyte separations in microfluidic devices (Schneegass et al., 2001). Further, a two-step process could be utilized to eliminate potential interactions of Rhodamine B dye with chemicals of interest.As the first step, a set of devices would be used with a dye solution to calibrate the temperature difference versus the microwave power characteristic of the device, and an identical device would be later used without the dye solution for performing biological or chemical studies. Alternatively, an electronic temperature sensor such as a thermocouple or resistance thermometer could be integrated into the device at a convenient reference location along the channel for optical calibration. Figure17plots the temperature as a function of time at one location along the microfluidic channel for a 1 s duration pulse of approximately 1 W of microwave power applied to the device. Substantially, more power (about 1 W from the amplifier) was required to raise the temperature of the fluid to 46 ◦C in 1 s than would be required to hold it at this temperature for an additional second as might be required in practical applications. It would be much easier to add feedback control of the microwave power if the temperature at a reference location was measured electronically rather than optically even if Rhodamine B or some other fluorescent dye was compatible with the other chemicals in the microchannel.
Transient temperature response of the integrated microfluidic device. A temperature of 46 0C was obtained at some locations in the microchannel with 1W of microwave power at the output of power amplifier for 1s. The fact that the temperature did not reach a steady state value in this time shows that considerably less power would be required to hold the temperature constant for a second. The addition of feedback control and a higher power amplifier would facilitate higher temperatures, a faster rate of increase in temperature, as well as the capability to hold the fluid temperature constant for a short period of time without raising the device temperature significantly.
Finally, the growing concern that exposure to microwaves can be harmful to living cells may limit the ability to operate highly integrated lab-on-a-chip devices containing living microorganisms in conventional microwave ovens. On the other hand, the microwave field decreases rather rapidly away from a properly designed microscale microwave generator, potentially allowing live organisms and microwave transducers to co-exist on a lab-on-a-chip device. The approach explained to establish temperature gradients appears to be especially well suited for thermal gradient focusing methods for analyte separations of cell metabolites in lab-on-a-chip devices. Other potential applications of integrated microwave heaters include cell lysis and PCR (Liu et al., 2002), as mentioned previously. The localized nature of on-chip microwave heating means that separate microwave heaters optimized for these different tasks could also co-exist on a single lab-on-a-chip device. Therefore, it is believed that the technique outlined here will facilitate the application of microfluidics to other biological and chemical applications requiring spatial temperature gradients as well as to temperature gradient generation.
The ability to rapidly and selectively control temperature within microchannel environment is crucial for many fluidic applications including high-efficiency PCR and temperature induced cell lysing. In this chapter, localized microwave dielectric heating of fluids at micrometer scale geometry using integrated planar microwave transmission line as a power source has been presented. The measured temperature increases with increasing frequency is in agreement with theory. The device offers several advantages. It is simple, easy to use and fabricate. The planar structure of the transmission line used as a power source lends itself to easy integration with the microchannel and allows for optical integration of the microchannel with widely used fluorescence microscopy techniques. The performance of the CPW for heating could be substantially improved by: applying high power pulses over shorter heating times, using a lower thermal diffusivity substrate than glass, and increasing the gap width and thickness of the CPW conductors.
A microwave power absorption model to understand power distribution through the device and to differentiate microwave heating of the fluid from conductive heating of the fluid because of microwave power absorption in thin-film CPW conductors has been presented. Based on the fitting of the experimental data using the power absorption model, it can be stated that the temperature rise of fluid is predominantly due to the absorbed microwave power. It is believed that this model can be useful for evaluating the performance of various complex and lossy transmission line configurations, such as CPW or microstrip lines, for heating fluid in the microchannel environment. Tt is believed that the microwave dielectric heating approach will be of particular use in rapid thermocycling applications and will lead to new applications exploiting heating in microfluidic environment. Such heaters are potentially very useful for single use, disposable, and integrated microfluidic systems.
The integrated microwave microstrip transmission line is also very attractive to generate temperature gradients rapidly and selectively in a microfluidic device. The shape of the temperature profile can be adjusted by varying the microwave excitation frequency and the amplitude of the profile can be adjusted by varying the microwave power. With this technique, the temperature gradients can be established locally and selectively by positioning the transmission line in the region of interest over the fluidic network. This device offers several advantages. Because the heating elements are integrated with the microchannel, this device offers a portable platform for generating spatial temperature gradients. The device is simple, easy to integrate and use with microfluidic channels, and allows for high frequency operation. The heating elements are easy to fabricate and the fabrication method is transferable to other microfluidic substrates. Reducing the thickness of the copper electrodes would provide larger temperature changes within the microchannel. This approach can be scaled for high throughput studies by fabricating multiple transmission lines in parallel. This approach to establish temperature gradients would be especially well suited for field gradient focusing methods for analyte separations. It will also facilitate the application of microfluidics to a multitude of other biological and chemical applications requiring spatial temperature gradients.
Authors acknowledge the contributions of SiddarthSundaresan in the early part of this work on microwave dielectric heating of microfluidic devices.
With the growing concerns on global warming and energy prices, the demand for environmentally friendly vehicles with better fuel efficiency is increasing [1, 2, 3]. These issues can be addressed by reducing car weight, lowering travel resistance, advancing drive-train efficiency, developing new sources of power, and so on. Vehicle weight reduction using advanced lightweight structural materials, such as Mg, Al, and Ti, is considered as one of the most promising strategies to address these issues [4, 5, 6, 7, 8, 9, 10]. Generally, for every 10% weight reduction, the specific fuel consumption could reduce by 3–7%, while maintaining the same functionality [11, 12]. Thus, the use of lightweight alloys as structural materials is considered as the factor for development of aerospace and automotive manufacturing sectors in the future. To achieve lightweight, safety, and low cost, the multi-material structure using steels, Al, Mg alloys is considered to be efficient [9]. Therefore, effective dissimilar joining process of such light metals and steels is essential.
As the lightest structural material, Mg alloys receive great attention due to their high specific strength, sound damping capabilities, hot formability, good castability, recyclability among others [13, 14, 15, 16, 17, 18]. Potential applications of Mg alloys in an automobile include seat components, bracket carrier, roof, bonnets, cylinder head, wheels, etc. [8, 19]. Steel is currently the automaker’s material of choice, due to its inherent properties, including high strength and toughness, good ductility, and low cost [8, 20, 21, 22]. Recently, it has been demonstrated through the next-generation vehicle project that stainless steels are promising candidates for vehicle construction, and they can be used replaced carbon steels, especially in crash-relevant components such as door pillars.
Therefore, for practical applications in automotive industries, Mg alloys will have to be joined with existing steel parts. Recently, many automotive components have been produced using a combination of Mg alloys and steels, but the major issues arise from the joining techniques and corrosion of the joined parts [23, 24, 25, 26]. Thus, attaining reliable Mg/steel hybrid joints is paramount for facilitating lightweight industrial fabrication and expanding the industrial applications of Mg alloys in automotive industries [21, 27, 28, 29].
Joining Mg alloys directly to steel is extremely difficult because of the huge differences in their physical and metallurgical properties, the lattice mismatch between Fe and Mg is very large and there is almost zero solubility between Mg and Fe [27, 29, 30, 31, 32, 33, 34, 35]. Hence, an appropriate technique that overcomes the aforementioned problems is very much desired.
Generally, a successful joint between Mg and steel can be achieved by inserting an intermediate material at the interface or diffusion of alloying elements from the BM. At present, several authors have focused on joining magnesium alloys to different grades of steel, using various welding technology, such as friction stir welding (FSW), ultrasonic spot welding (USW), diffusion and eutectic bonding, resistance spot welding, laser welding brazing, laser-TIG hybrid welding and gas metal arc weld-brazing. In these studies, various interlayer elements and alloys such as Zn, Ni, Cu, Cu-Zn, Sn, Al, and Ag have been explored. In contrast to direct joining of magnesium to steel, which is mainly a mechanical bonding, with insertion of the interlayer elements, formation of intermetallic phases or solid solutions between Mg and the interlayer and also the interlayer and Fe indicated that metallurgical bonding is achieved. However, the joint performance and the interfacial bonding achieved depend significantly on the IMC phase formed [31, 36, 37, 38]. To control the morphology and existence state of the intermediate phase, the selection of suitable interlayer material and joining techniques are essential. Generally, choosing the suitable interlayer for joining Mg alloys to steel largely depends on the interlayer composition that gives excellent wetting and bonding without generating thick layers of hard and brittle IMCs at the joint interface [31, 35, 39, 40, 41]. Moreover, when choosing the joining process that will be used, minimization of the thickness of any brittle intermetallic compounds along the interfaces of the magnesium alloy-interlayer-steel joint and minimization of intermixing between the Mg and Fe in the molten-state are the main factors that must be considered [8, 21, 42, 43].
Currently, a great deal of research has been conducted on the interface characteristics and mechanical performance of Mg alloys to steel joints, particularly under static loading. Under optimized processing conditions, excellent static strength has been achieved, even surpassing that of Mg alloy base metal with insertion of Ag, Cu, and Ni intermediate elements [38, 44]. However, few experiments have been carried out on the corrosion behavior of the jointed parts and the joints performance under dynamic loading [45, 46, 47, 48].
With the continuously increasing usage of Mg alloys in industries and the large number of potential applications of Mg/steel hybrid structures, two of the specific areas of concerns for broader utilization of magnesium alloys are reliable joining techniques and corrosion behavior of the joined parts. To better understand and address these challenges, there is a need to comprehensively review the research conducted so far and provide the most efficient strategies to address the challenges. This paper presents a review on Mg alloys/steel joining techniques, with focus on the techniques used to control the morphology and existence state of intermetallic compound (IMC) and improving mechanical properties. The general motives behind this review are to obtain a better understanding on the weldability issues associated with joining magnesium alloys to steel. It would also establish global, state-of-the-art welding techniques of Mg alloys to steel.
Some of the inherent properties of Mg include high thermal conductivities and coefficients of thermal expansion, large solidification temperature ranges, strong tendency to oxidize, low viscosity and surface tensions, high solidification shrinkage, low melting and boiling temperatures, a tendency to form low melting point constituents and high solubility for hydrogen in the liquid state [8, 30, 49]. It is obvious that the properties of Mg differ significantly from those of Fe. For instance, the melting points of magnesium and iron are 649°C and 1536°C, respectively. This wide discrepancy in melting points makes it very difficult to melt the base materials at the same time as might be required in fusion-welding process [21].
In addition, the crystal structure of Iron at room temperature is body-centered cubic (BCC), whereas that of magnesium is close-packed hexagonal (HCP). Crystallographic analysis has shown that the lattice mismatch of Fe and Mg is very large [34, 50, 51]. Although the welding process itself is a non-equilibrium process, phase diagram has always been an effective tool to predict the reactions formed during welding process and serves as a reference to examine the feasibility of achieving a metallurgical bonding between the metals. According to the Mg/Fe binary phase diagram, the maximum solid solubility of iron in magnesium is 0.00043 wt.% while that of magnesium in iron is nil, and the Mg concentration at the eutectic point is estimated to be less than 0.008 at.% [34, 52, 53, 54]. Therefore, magnesium and steel are immiscible (neither the formation IMC nor atomic diffusion occurs between them after solidification), thereby presenting difficulty in joining them together.
In recent years, numerous techniques have been applied to bond Mg alloys to various grades of steels. These techniques can be broadly classified into solid-state joining (friction stir welding, ultrasonic spot welding, diffusion-welding processes) and fusion welding (resistance spot welding, laser welding brazing, laser hybrid welding, and arc welding). Review of the literature reveals that metallurgical bonding along the Mg/steel interface can be achieved with addition of suitable interlayers (which possess a substantial solid solubility in both Mg and Fe) or inter-diffusion of the alloying element from the BM. Therefore, the joint quality is significantly influenced by the interlayer characteristics (forms, thickness, and compositions). Among the joining techniques, a variety of thin interlayers such as Zn, Cu, Al, Ni, Sn, Cu-Zn, and Ag has been reported to improve the interfacial reaction between magnesium alloys and steel. In this section, the potential of several methods for joining magnesium and steel will be discussed.
Solid-state joining technology has been applied to bond Mg alloys to steel and get high-quality joints than fusion-welding processes because of the added advantage of minimal oxidation because of the solid-state nature of the process. Solid-state joining processes, such as friction stir welding (FSW), ultrasonic spot welding (USW), and diffusion and eutectic bonding, have been used to join Mg alloys to steel. Generally, for solid-state bonded Mg alloys-interlayer-steel joints, the joint performance is influenced by the intimate contact between the dissimilar materials, and the microstructure, particularly the formation of IMCs [55, 56].
FSW is a solid-state welding technique invented by Thomas et al. [57]. The combined action of pressure and stirring during the FSW led to mutual diffusion of the alloying elements from the BM, which promoted metallurgical bonding at the interface and improved the joint performance. Some of the unique advantages of FSW include low distortion and residual stresses due to low heat input and absence of melting, filler metal is not required and the heat efficiency is very high relative to traditional fusion-welding processes [58, 59]. Joining Mg alloys to steel by FSW has been extensively studied.
Watanabe et al. [60, 61] investigated the weldability of AZ31 Mg alloy to uncoated SS400 steel joints by FSW. Under optimum joining condition (0.1 mm tool pin offset toward steel plate, 1250 rpm pin rotation speed, and welding speed of 100 mm/min), a joint with maximum strength of about 70% of the Mg BM was obtained. The low joint strength was associated with insufficient plasticization and presence of steel fragments in the Mg matrix. Considerable number of authors observed that the presence of zinc coating on the steel surface played an important role in the bond formation between the Mg alloys and steel [21, 27, 56, 62, 63]. For instance, Schneider et al. [63] and Jana et al. [27] joined AZ31B alloy to Zn-coated steel by FSW. It was found that the Zn coating enhanced the bondability of the Mg alloy/steel. The authors noted that the strength of the FSW welded AZ31B/galvanized steel was significantly superior to that of AZ31B/uncoated steel. The presence of Zn coating promoted the formation of liquid low melting Mg-Zn eutectic products at the interface. The liquid products, broken oxides, and other contaminants were forced out of the joining interface by the high pressure produced by the tool, exposing the fresh interfaces. As a result, mutual diffusion between magnesium alloy and steel was achieved.
Friction stir spot welding (FSSW) a variant of FSW, has also been used to join Mg alloys to steel. Liyanage et al. [29] joined AM60 to DP600 dual-phase steel by FSSW, and the welds showed no evidence of intermetallic formation. They reported that a Zn layer on DP600 steel resulted in melted eutectic material (αMg + MgZn) and cracking in the joints. The feasibility of joining 3 mm thick AZ31 Mg alloy to 1 mm 302 stainless steel by FSW was also reported [64]. The results showed that the combined action of pressure and stirring led to mutual diffusion of the alloying elements from the BM at the interface. Under optimum condition, the joints shear strength reached a maximum of 96.3 MPa. However, void and microtype defects at the interface were observed.
Joo et al. [65] reported that an acceptable AZ31B/SS400 steel joints with higher strength, sufficient material flow and tool wear reduction were obtained using hybrid gas tungsten arc welding (GTA) and friction stir welding. The tensile strength of the hybrid friction stir welds increased to 237 MPa about 91% of the Mg BM, compared to 226 MPa for conventional friction stir welds.
The prior research proved that refill friction stir spot welding (RFSSW) has many advantages for joining of Mg alloys/steel dissimilar welds [48, 66, 67]. Zhang et al. [67] joined 3 mm AZ31B to 1 mm galvanized steel joints by friction stir keyholeless spot welding (FSKSW) and reported that the stacking sequence of the workpieces played a significant role in determining the mechanical properties. Under optimum joining condition, the maximum joint strength of 8.7 kN was achieved. Furthermore, 1.53 mm ZEK100 Mg alloy was welded to 1 mm Zn-coated DP600 steel with 10 μm Zn coating by RFSSW [66]. The authors observed that the sleeve did not plunge into the bottom steel. A thin interfacial layer with thickness of <100 nm identified as FeAl2 by TEM was observed at the interface, which accommodates bonding between the immiscible Mg and Fe and appeared to have originated from Zn-based galvanized coating on steel. Under optimum process parameters (tool speed of 1800 rpm, welding time of 3.0 s, and penetration into the upper ZEK100 of 1.5 mm), the joints shear strength of 4.7 kN was achieved.
However, numerous studies focused on characterizing the Mg alloys to steel joints under dynamic loading condition [20, 48, 68]. For example, the fatigue behavior of FSW-produced by AZ31 and two types of Zn-coated steels (HSLA steel or mild steel (MS)) lap joints has been investigated [20]. It was found that the performance of friction stir welded joints under fatigue load is limited due to ‘hook’-like features formed along the magnesium/steel interface, which act as stress raisers. Uematsu et al. [68] investigated the static and dynamic behavior of dissimilar lap joining of 2 mm AZ31 Mg alloy to 2 mm cold-rolled low carbon steel by FSSW. The results showed that fatigue crack grew through the interface, regardless of load levels. The authors noted that the effective nugget size could be the controlling factor of the fatigue strengths of dissimilar welds, and it is essential to increase the effective nugget size to improve the fatigue performance of dissimilar welds. Shen et al. [48] compared the static and dynamic behavior of 1.5 mm ZEK100 Mg alloy/0.9 mm galvanized DP600 steel dissimilar spot welds to Mg/Mg similar welds produced by RFSSW. It was observed that the static and dynamic behaviors of the magnesium/steel welds were superior to that of Mg/Mg similar spot welds. The higher joint performance observed for Mg to Zn-coated steel was associated with an increase in effective bonded area, compared to Mg/Mg spot welds due to the presence of displayed Zn-coated layer. Furthermore, the analysis of the dynamic behavior of the Mg alloys to galvanized steel joints revealed that the Zn brazing quality directly influences the fatigue life. Therefore, optimization of the welding parameters to facilitate this brazing to magnesium is necessary [48].
Comparison of the Mg alloys/steel joints maximum tensile shear strength produced by FSW and FSSW are shown in Table 1. In FSW welding, prior studies placed Mg alloys as the top sheet while the tool plunge depth was carefully controlled to avoid contacting the steel tool to the bottom ferrous substrate. However, this arrangement resulted in a low joint strength [64]. Interestingly, with recent RFSSW, the sleeve did not lunge into the bottom steel, which significantly increased the effective bond area and improved the joints performance [66, 67, 68, 69, 70, 71]. During FSW and FSSW, the processing heads impose size and shape limitation, the process is best used with long and straight welds, and keeping the interlayer at the interface between the steel and Mg alloy is very difficult due to the stirring action of the pin and material flow with high plasticity along the interface. Thus, limited the wide range of application of these techniques in industries [48, 72]. The comparison of the joint properties reveals that good static weld strength can be obtained between magnesium alloys to galvanized steel by a diffusion and braze-bonding mechanism [48, 66]. Most studies focused on using Zn interlayer, and there is a need to experiment with other interlayers. Furthermore, no study focused on the corrosion behavior of the joined parts.
Techniques | Materials | Joint design | Transition material | Maximum tensile shear strength (MPA) | Failure mode | References |
---|---|---|---|---|---|---|
FSW | 2 mm AZ31B-O/2 mm SS400 mild steel | Butt (Offset 0.1 mm toward steel) | No interlayer | 178.5 MPa | Interfacial | [60, 61] |
FSW | 1.6 mm AZ31/0.8 mm Zn-coated steel | Lap (Mg on top) | Zn coating | 3.7kN | Interfacial | [21, 62] |
1.6 mm AZ31/0.8 mm Brushed finished steel | Uncoated | 2.9kN | Stir zone | |||
FSW | 2.33 mm AZ31B/1.5 mm HDG steel | Lap (Mg on top) | Hot dip Zn coating | 6.3 ± 1.0 kN | Interfacial | [27] |
2.33 mm AZ31/0.8 mm HSLA electrically galvanized steel | Electro-galvanized Zn coating | 5.1 ± 1.5 kN | ||||
FSW | 2 mm AZ31B/2 mm DX54D | Lap (Mg on top) | Uncoated | 98 MPa | Stir zone | [63] |
Zn coating (15 μm thick) | 158 MPa | |||||
FSSW | 1.2 mm AM60/1.8 mm DP600 | Lap (Mg on top) | Zn coating | 2.4 ± 0.5kN | AM60 BM | [29] |
FSSW | 2 mm AZ31 Mg alloy/2 mm cold-rolled low carbon steel | Lap (Mg on top) | No interlayer | 32 MPa | Interfacial | [68] |
FSW | 3 mm AZ31/1 mm SUS302 | Lap (Mg on top) | No interlayer | 96.3 MPa | Stir zone | [64] |
GTA-FSW | 3 mm AZ31B/3 mm SS400 | Butt | No interlayer | 237 MPa | Interfacial | [65] |
FSW | 226 MPa | |||||
FSKSW | 3 mm AZ31B/1 mm Q235 | Lap (Steel on top) | Zn coating | 8.7kN | Not reported | [67] |
RFSSW | 1.55 mm ZEK100/1 mm DP600 | Lap | Zn coating | 4.7kN | Interfacial | [66] |
RFSSW | 1.5 mm ZEK100/0.90 mm DP600 | Lap | Pure Zn coating (10 μm thick) | 3.6kN | Interfacial | [48] |
Comparison of the Mg alloys/steel joints maximum tensile shear strength produced by FSW and FSSW.
USW is also a solid-state welding technique that generates coalescence through a concurrent application of localized high-frequency vibratory energy and slight clamping force [73]. At present, the research conducted on joining magnesium alloys to steel using USW is limited.
Santella [74, 75] joined 1.6 mm thick AZ31B-H24 to 0.8 mm HDG mild steel by USW. The authors noted that the presence of Zn improved the bonding mechanism, but the Mg-Zn phases were completely squeezed from the spot weld and only thin Al5Fe5 phase was formed at the interface. Under optimum welding parameters, a joint with maximum lap shear strength of 4.2 kN was achieved. In another related study, Patel et al. [73] also noted that Mg and Zn combined to form Mg-Zn IMCs, while Fe and Zn combined to form a solid solution to create the weld joint. The results of these studies could suggest that no melting on the steel side occurs during USW. In comparison, Patel et al. [76] observed that the shear strength of the magnesium alloy/bare steel with the addition of Sn interlayer was higher than that of magnesium alloy/bare steel and magnesium alloy/galvanized steel joints, due to the solid solutions of Sn formed with magnesium and iron, as well as Sn and Mg2Sn eutectic.
On the other hand, it was demonstrated that corrosion could impair the mechanical performance of Mg alloy/steel USW joints [46]. However, the details of corrosion mechanisms required further study.
Table 2 compares maximum tensile shear strength of the Mg alloys/steel joints produced by USW. The USW techniques involved the use of an interlayer to achieve interfacial reactions. The highest joint strength (about 88% of Mg/Mg ultrasonic spot weld) was obtained using Sn interlayer due to the solid solutions of Sn formed with magnesium and iron, as well as Sn and Mg2Sn eutectic structure. Therefore, using Sn interlayer resulted in better joining mechanism and mechanical performance and is thus more suitable [76]. Thus, choosing of suitable interlayer is essential for successful joining. The possibility of using different transition materials should be explored. Furthermore, studies on dynamic and corrosion behavior of the USW joint parts should be given attention.
Techniques | Materials | Joint design | Transition material | Maximum tensile shear strength | Failure mode | References |
---|---|---|---|---|---|---|
USW | 1.6 mm AZ31B-H24/0.8 mm HDG mild steel | Lap | Zn coating (9 μm thick) | 4.2kN | Through the AZ31 BM | [74, 75, 77] |
USW | 2 mm AZ31B-H24/0.8 mm HSLA | Lap | Zn coating (10 μm thick) | 47 MPa | Interfacial (cohesive failure) | [76] |
Uncoated | Sample failed during specimen mounting | — | ||||
Uncoated with Sn interlayer (50 μm thick) | 71 MPa | Partial nugget pull-out |
Comparison of the Mg alloys/steel joints maximum tensile shear strength produced by USW.
Diffusion methods have been used to successfully join both similar and dissimilar materials combinations, including Mg alloys/steel [37, 78]. During the diffusion process, formation of uniform and thin IMC along the Mg alloy/steel interface is the key for successful bonding. The number of research suggested that interfacial bonding could be achieved by either addition of interlayer or some alloying elements in the Mg BM. The benefits of using Cu [78, 79, 80], Ni [37, 80], and Ag [44, 81] interlayers during diffusion bonding of Mg alloy/steel have been demonstrated.
Tachibana et al. [82] studied the influence of the Zn insert on the bondability of Mg/steel lap joints. It was found that the AZ31 and cold-rolled steel plate (SPCC) could not bond due to the oxide films formed on the AZ31 that prevented the bonding, while AZ31/Zn-coated steel (GI) was bonded successfully. The presence of zinc coating enhanced the bondability of Mg alloy/steel and removed the oxide films on AZ31. The weldability of 5 mm AZ31 Mg alloy to 1 mm thick 316 L steel joints using a diffusion brazing process with addition of Cu and Ni interlayers was also reported [37, 79, 80, 83]. Solid-state diffusion of the interlayer into the magnesium alloy, eutectic formation, and the formation of ternary IMCs was observed at the joint interface. The interfacial reaction was intense in the liquid state, inducing the excessive formation of brittle and thick IMC layers, which was detrimental to the joint strength. The maximum joint strength of 57 MPa (69% of that of AZ31 BM) with Cu interlayer was obtained compared to 32 MPa for Ni added joints. The high interfacial bond obtained for Cu-added joint was associated with confined intermetallics at the bonded interface compared to dispersed intermetallics for Ni added joint [80].
Some authors focused on bonding magnesium alloys to steel using reactive transient liquid phase bonding (rTLP) to improve the joints strength between dissimilar metals. During the rTPL process, eutectic melting and subsequent isothermal solidification occurred between the interlayer and the magnesium, while the formation of a thin continuous layer between the melt and the steels resulted in interfacial bonding of the steel with the magnesium substrate [44, 81]. The bondability of AZ31 to low carbon steel with the addition of Ag interlayer using rTPL process showed that isothermal solidification of the eutectic melt was formed at the Mg alloy side through the diffusion of Ag into the magnesium BM. Thin and uniform Fe2Al5 layer was observed at the steel side, which significantly improved the joint strength to 201 MPa [44, 81]. In contrast, coarse, non-uniform IMC intermittently formed at the interface without Ag interlayer, which deteriorates the joint performance.
Table 3 gives a comparison of the Mg alloys/steel joints maximum tensile shear strength produced by diffusion and eutectic bonding. The literature reveals that the interlayer material has significant influence on the bondability of the Mg alloys to steel by diffusion and eutectic bonding process. The use of Cu, Ni, and Ag as intermediate elements has been studied. The major challenge associated with this technique is that the formation of ternary IMCs which could not be controlled and have detrimental effects on the joint performance [80]. A comparison of the joints strength shows that excellent static strength of Mg/steel joints has been achieved using rTPL techniques, even surpassing that of AZ31B Mg alloy BM with addition of Ag interlayer [44]. The rTPL unique qualities of short process time, coupled with forming a thin and continuous intermediate layer through the formation of a transient liquid interlayer, were responsible for the high joint performance obtained. The possibility of improving the joint performance using more interlayers should be explored.
Techniques | Materials | Joint design | Transition material | Maximum tensile shear strength (MPa) | Failure mode | References |
---|---|---|---|---|---|---|
Diffusion bonding | AZ31/SPCC | Lap | Uncoated | — | No reported | [82] |
AZ31/GI | Pure Zn coating (6 μm thick) | 40 | ||||
AZ61/GI | Pure Zn coating (6 μm thick) | 70 | ||||
Diffusion brazing | 5 mm AZ31/1 mm 316 L | Lap | Pure Cu (20 μm) | 57 | Mg BM | [80] |
Pure Ni (20 μm) | 32 | Steel/Ni interface | ||||
rTPL bonding | AZ31B/Low carbon steel | Lap (Mg on top) | — | 40 | Interfacial | [44, 81] |
Pure Ag (1 μm) | 201 | Mg BM |
Comparison of the Mg alloys/steel joints maximum tensile shear strength produced by diffusion and eutectic bonding.
Fusion welding involves joining the surface of the materials through melting and solidification to produce the bonding. Fusion-welding technologies based on resistance spot welding [4, 32, 84, 85, 86] laser braze [41, 43, 87, 88, 89, 90, 91, 92], laser hybrid [33, 35, 36, 38, 39, 40, 47, 93, 94, 95, 96, 97, 98] and arc welding [72, 99, 100, 101, 102] have been investigated for joining magnesium alloys to steels. In general, the insertion of an interlayer or mutual diffusion of alloying elements from the BM has been adopted to improve interfacial bonding. The addition of suitable interlayer improves the spreadability and the nucleation of magnesium on steel.
RSW is the most widely used welding technology in the auto industry [103] due its low cost, high speed, ease of operation, and automation [17, 32, 86]. Despite the inherent advantages of RSW, very limited work has been published in joining Mg alloy to steel. This include AZ31B Mg alloy/Zn-coated DP600 steel [32], AZ31 Mg alloy/HDG steel with pre-coated nanoscale Fe2Al5 layer [34], AZ31B-H24 Mg alloy/HDG HSLA steel [4], AZ31B Mg alloy/HDG HSLA steel [84] and AZ31B Mg alloy/electro-galvanized DP600 steel [86].
Most of the works focused on joining magnesium alloys to galvanized steel. Liu and his co-workers developed a novel technique (asymmetric electrode) to lap weld 1.5 mm AZ31B to 1.2 mm HDG DP600 steel successfully by RSW [32]. It was found that the Zn interlayer was squeezed out of the bond region producing deal condition for intimate contact of fresh Mg and steel surfaces. The joining mechanism consisted of braze welding, solid-state bonding, and soldering. Under optimum parameters, a joint with tensile shear strength of 5.0 kN was obtained. Xu et al. [4] compared the microstructure and mechanical performance of AZ31B to HDG HSLA steel joints by RSW and weld-bonding (WB), which combines the RSW and adhesive bonding. It was found that the peak shear load and energy absorption of the weld-bonded magnesium to steel joints were higher than that of resistance spot welded magnesium to steel joints. In another similar study, AZ31B was joined to HDG HSLA steel by RSW under dynamic loading [84]. It was found that the microstructure of the Mg/steel spot welds was different from that of Mg/Mg spot welds, but owing to similar crack propagation and failure mode, both welds had an equivalent fatigue resistance. Interestingly, Feng et al. [86] joined AZ31 to electro-galvanized DP600 steel by RSW process with and without HDG Q235 interlayer. Contrary to the previous studies [4, 32, 84] that used hot-dip Zn coating, the thin and compact features of electro-galvanized zinc layer prevented the zinc-coated layer on the steel to be squeezed out of the nugget. However, with insertion of HDG Q235 interlayer, the zinc-coated layer was squeezed out of the nugget and a peripheral soldered region was formed during the welding process, which significantly improved the joint tensile shear load from 4.14 kN to 5.49 kN. The feasibility of joining AZ31B Mg alloy to DP600 steel via pre-coated nano-scaled Fe2Al5 interlayer was also investigated [34]. The analysis of the interface characteristics revealed that metallurgical bonding was achieved due to the formation of the semi-coherent interfaces of Mg/Fe2Al5/Fe with well matching lattice.
However, RSW of Mg alloy to stainless steel is more challenging because of the absence of any Zn coating. However, Mg alloy to stainless steel joints has been reported [85, 104]. Min et al. [104] investigated the 0.4-mm thick AZ31B sheets, and 0.4-mm thick 443 ferritic stainless steel welded joints using the RSW with 443 ferritic stainless steel cover plates. It was found that Fe-Al IMC layer was formed at the interface, and the molten Mg could wet the surface of the interface layer. However, cracking was observed in the nugget. The crack was associated with the possible thermal behavior of various elements in the nugget during spot-welding process. Recently, Manladan [85] compared the microstructure and mechanical performance of 1.5 mm thick AZ31 Mg alloy/0.7 mm thick 316 L austenitic stainless steel joints by RSW and resistant element welding (REW). In comparison with two-zone FZ, consisting of peripheral FZ on the ASS side and main FZ observed for REW, the RSW joints were produced through welding-brazing mode, in which the Mg alloy melted and spread on the solid steel, forming the nugget only on the Mg side. The RSW produced the weak joint with a peak load of 2.23 kN and energy absorption of 1.14 J, whereas REW produced the strong joint with a peak load of 3.71 kN and energy absorption of 10.2 J.
Generally, in the RSW process of Mg alloys, large electric currents are always needed due to its high electrical and thermal conductivity, which commonly results in expulsion and electrode stick. In addition, RSW created only a localized joint, which may not be particularly strong [105].
A comparison of the Mg alloys/steel joints maximum tensile shear strength produced by RSW is shown in Table 4. It can be seen that limited research has been conducted on magnesium alloys/steel. The presence of zinc layer was crucial for successful welding of magnesium to steel. The predominant failure mode observed is interfacial (IF). This is the kind of failure mode commonly observed when conducting tensile shear tests on spot welds, in which the crack propagates through the nugget. A comparison of the joints performance shows that good static strength has been achieved, almost 95% Mg/Mg spot joint strength by RSW [32]. However, the research on the fatigue performance of Mg/steel dissimilar welds is still at its infancy due to the special geometry of the spot welds; it is hard to predict the crack initiation and propagation rate as reported by Liu et al. [84]. Among the RSW techniques, weld bonding produced the joint with highest mechanical resistance with joint failure on the Mg BM. Weld-bonding joining techniques has the advantages of low manufacturing costs, higher static and fatigue performance, and improved corrosion resistance [106, 107].
Techniques | Materials | Joint design | Transition material | Maximum tensile shear strength (kN) | Failure location | References |
---|---|---|---|---|---|---|
RSW | 1.5 mm AZ31/ 1.2 mm Zn-coated DP600 | Lap (Mg on top) | HDG Zn-coated (9 μm to 12 μm) | 5.0 | Interfacial failure (IF) mode | [32] |
RSW | 1.5 mm AZ31/ 1.2 mm HDG DP600 | Lap (Mg on top) | Bare steel | 0.0 | Not reported | [34] |
Fe2Al5 | 4.8 | Not reported | ||||
RSW | 1.5 mm AZ31B/0.77 mm HSLA steel | Lap (Mg on top) | HDG Zn-coated (11 μm) | 2.0 | Interfacial failure (IF) mode | [84] |
RSW & WB | 2 mm AZ31B-H24/0.7 mm HSLA steel | Lap (Mg on top) | HDG Zn-coated (11 μm) | RSW 4.80 WB 10.0 | IF (RSW) Mg BM (WB) | [4] |
RSW | 2 mm AZ31B/ 1.2 mm Electro-galvanized DP600 | Lap (Mg on top) | No transition material | 4.14 | IF | [86] |
HDG Q235 (0.6 mm) | 5.49 | IF | ||||
RSW & REW | 1.5 mm AZ31/0.7 mm 316 SS | Lap (Mg on top) | No transition material | RSW 2.23 | IF | [85] |
REW 3.71 | PO |
Comparison of the Mg alloys/steel joints maximum tensile shear strength produced by RSW.
Laser beam welding presents a viable option for welding Mg alloys to steel due to its versatility, high specific heat input, and flexibility [55, 108, 109, 110, 111]. Although fusion welding resulted in severe vaporization of Mg alloy at typical welding temperatures, the selection of optimum welding conditions is crucial for successful joining. Therefore, to control the severe vaporization of Mg, considerable number of authors concentrated on laser welding brazing and laser hybrid techniques.
Laser welding brazing (LWB) techniques offered additional advantages such as increased flexibility and adoptability when welding dissimilar metals [28, 91, 92, 112, 113]. To this end, LWB technique is suitable for joining dissimilar materials having large differences in melting points such as Mg/Ti [18, 114, 115, 116], Al/Ti [117], and Al/steel [118, 119]. In particular, welding of magnesium alloys to steel by LWB process was achieved with addition of third material or mutual diffusion of alloying elements. Thin interlayers such as Al [28, 120, 121], Ni [90, 113], Sn [31], Zn [41, 42, 87, 88, 91], and Fe-Al [41], have been used to improve the interfacial bonding between the immiscible Mg and Fe. Miao demonstrated the feasibility of joining 2.4-mm AZ31B Mg alloy to 1.7 mm Q235 steel by laser welding brazing process using high power CO2 laser without welding wire [122, 123, 124]. The analysis of the interface characteristics revealed that transition layer consisted mainly of IMCs, and metal oxides were observed at the interface. The compounds were identified by TEM as Al-rich phases, such as Mg17Al12, Mg2Al3, FeAl, and Fe4Al13 [124]. Although tensile strength of the butt joints could reach 182 MPa (81% of Mg alloy BM), but severe oxidation and vaporization of the magnesium alloy, coupled with immiscibility between magnesium and iron, led to weld defects such as spatters and porosity.
Therefore, to address the severe vaporization of the Mg, laser brazing or laser welding brazing with magnesium-based filler wire was proposed [28]. The benefits of using Al-12Si [28], Ni [113], Sn [31], and Zn [42] as transition material between Mg alloy to steel were explored by Nasiri and co-workers. It was found that the presence of the interlayer significantly improved the spreadability of the liquid magnesium-based filler on steel surface but deteriorated the joint performance because of the weak bonding of IMCs products formed along the interface.
However, several authors observed mutual diffusion of alloying elements when joining Mg alloys to different grades of stainless steel [92, 125, 126]. For instance, [92] compared the joint performance of lap welded 1.5 mm-AZ31B/1.5 mm-mild steel (MS) joints and 1.5 mm-AZ31B/1.5 mm 201 stainless steel (SS) joints produced by LWB. Mechanical bonding was observed for Mg alloy to MS joints, whereas for Mg alloy to SS joints, thin reaction layer identified as FeAl by TEM as shown in Figure 1. The Al diffusion from magnesium BM to the interface was accelerated by chemical potential induced by alloying elements of Cr and Ni was responsible for the interfacial reaction layer obtained.
Mg/201 stainless steel interface characteristics [
A comparison of the Mg alloys/steel joints maximum tensile shear strength produced by LWB is shown in Table 5. The selection of suitable interlayer is crucial for successful bonding. For instance, using Ni and Sn interlayers, which led to formation of the Fe(Ni) and Al8Mn5-Fe(Al) reaction products along the α-Mg-Fe interface, respectively, resulted in formation of strong interfaces with low mismatch strain energy and strong bonds. Therefore, using both Ni and Sn interlayers is recommended for dissimilar joining of steel sheet to magnesium sheet. Furthermore, the diffusion of the alloying elements in BM and the bonding mechanism were extensively studied. A comparison of the joints properties reveals that relatively good static strength of magnesium alloy to steel joints has been obtained [126]. However, the behavior of the Mg alloys/steel joint under dynamic loading is yet to be explored. Among the LWB techniques, dual-beam mode with flux produced joint with an excellent mechanical resistance. To further enhance the reliability of the joint and improve its performance, the possibility of using different interlayers should be explored.
Techniques | Materials | Joint design | Transition material | Maximum strength | Failure mode | References |
---|---|---|---|---|---|---|
Laser welding | 3 mm AZ31B/1.2 mm SP781 steel | Lap (Mg on top) | Zn Coating | 6182 N | AZ31B FZ & Transition zone | [43] |
Laser penetration brazing | 2.4 mm AZ31B/1.7 mm Q235 steel | Butt (0.6 mm offset on Mg) | No interlayer | 182 MPa | Interface | [122, 123, 124] |
Laser brazing | 2 mm AZ31B-H24/1 mm Al-12Si coated steel 2.4-mm- Dia Ti-Braze Mg 600 wire | Single flare bevel Lap (Mg on top) | Al-12 wt-% Si coating (20 ± 2 μm thick) | 767 ± 138 N | Interface | [28] |
Laser brazing | 2 mm AZ31B-H24/1 mm Al-12Si coated steel 2.4-mm- Ti-Braze Mg 600 wire | Single flare bevel Lap (Mg on top) | Pure Ni coating(5 μm) | 1506.3 ± 24.5 N | FZ | [113] |
Laser brazing | 2 mm AZ31B-H24/0.6 mm AISI 1008 | Lap (Mg on top) | Pure Sn coating (3.7 ± 0.7 μm thick) | 2064 ± 85 N | Steel BM | [31] |
Laser brazing | 2 mm AZ31B-H24/0.8 mm AISI 1008 | Lap (Mg on top) | Pure Zn coating (2.6 ± 0.5 μm thick) | 1086.4 ± 150.2 N | Interface | [42] |
Laser welding brazing | 1.5 mm AZ31B-H24/1.5 mm DP980 | Lap (Mg on top) | uncoated | 160 N/mm | Interface | [87, 88, 91] |
Zn coated (10 to 15 μm) | 228 N/mm | |||||
Laser welding brazing | 1.5 mm AZ31B-H24/1.5 mm DP980 with 1.2 mm AZ31 filler | Lap (Mg on top) | uncoated | 190 N/mm | Interface | [41] |
Zn + Fe-Al Phase | 180 N/mm | Interface | ||||
Zn coating (10 μm) | 160 N/mm | Interface | ||||
Fe-Al coating (0.9 μm) | 240 N/mm | Weld Seam | ||||
Laser welding brazing | 1.5 mm AZ31/1.5 mm 22MnB5 with 1.2 mm AZ61 filler | Lap (Mg on top) | AlSi10Fe3-coating | 3090 N | AZ61 filler | [121] |
Laser welding brazing | 1.5 mm AZ31B/1 mm Q235 | Lap (Mg on top) | Al (0.3 mm) | 133 N/mm | FZ | [120] |
Laser welding brazing | 1 mm AZ31B-H24/1 mm Q235A with 1.2 mm AZ92D filler | Lap (Mg on top) | Ni coating (4.5 ± 0.5 μm) | 190 N/mm | FZ | [90] |
Laser Welding brazing | AZ31B/mild Steel | Lap (Mg on top) | No interlayer | 142 N/mm | Interface | [92] |
AZ31B/stainless steel | 270 N/mm | Mg FZ | ||||
Laser welding brazing | 1.5 mm AZ31B-H24/1.5 mm 201 stainless steel and 2 mm AZ31 Filler | Lap (Mg on top) | No interlayer | 274.5 N/mm | Mg HAZ | [125, 126] |
Laser offset welding | 3 mm AZ31/3 mm AISI 316 | Butt (3 mm Offset on Steel) | No interlayer | 100 MPa | AZ31 BM | [30] |
Comparison of the Mg alloys/steel joints maximum tensile shear strength produced by laser welding brazing.
The excessive evaporation of magnesium during fusion welding can be overcome through the method of TIG-assisted laser process [33]. Generally, the addition of TIG could improve absorption of laser power and penetration of molten pool. During laser-TIG process, the TIG torch melts the magnesium, whereas, the laser is used to create deep penetration into the steel [36, 39]. Several authors reported that conventional fusion-welding technology such as TIG or laser welding alone could not be competent for joining of magnesium to steel [33, 89, 94]. For instance, [33, 89] demonstrated during TIG welding of Mg alloy to steel with higher heat input, either the magnesium alloys melt but the steel remained in solid state or the steel melt while blowholes formed in the magnesium alloys. In both cases, the bonding between the immiscible couple could not be obtained. Similarly, for conventional laser-welded magnesium alloys to steel joints, the immiscible materials could be joined with poor weld appearance and poor strength, coupled with large amount of electricity consumed by laser due to low absorptivity of magnesium alloys at room temperature [127]. For TIG-assisted laser process, the reflectivity of the magnesium to laser was reduced and thus the absorption of laser beam improved, creating a deeper penetration in the steel [33, 35, 128]. Consequently, laser-TIG process offers great potential for improving the joint performance for both similar and dissimilar metal welding [33, 39, 40, 89, 129, 130].
Like other joining techniques, interfacial bonding between magnesium alloy to steel could be achieved by insertion of third material or mutual diffusion of alloying elements from the BM [95]. Therefore, the benefits of using Cu [35, 39, 40], Ni [35, 36, 40, 93, 96], Sn [94], Zn [89], Cu-Zn [40, 97] to bond magnesium to steel had been extensively studied. These interlayers formed Mg2X IMC (where X is the interlayer elements) and a solid solution of interlayer in iron along the joint interface, which consequently enhanced the joints mechanical strength [40].
Liu examined the weldability of AZ31B/304 SS by laser-GTA process. A transitional zone consisting of Mg-Fe and magnesium diffusion into the matrix of iron in the form of oxide was observed at the interface. The formation of the complex MgO, ZnO, Fe2O3, or Al2O3 oxides deteriorates the joint strength [39, 94]. Furthermore, the use of laser-TIG techniques to join AZ31B and Q235 steel with Ni, Cu, Sn, and Cu-Zn interlayers was also explored [35, 36, 38, 39, 40, 93, 94]. These interlayers were heated and melted to react with magnesium and steel, and formed a transitional layer in the FZ and solid solution along the steel side. The analysis of the strengthening mechanism revealed that with the addition of suitable interlayers, the joint shear strength could reach a significantly high value or even surpasses Mg alloy BM.
Generally, the corrosion behavior of magnesium alloys is affected by the microstructural variation imposed by welding process [27, 43, 56, 63, 64, 125, 126, 131]. For similar Mg/Mg welds, the grain refinement imposed by welding process was reported to improve the corrosion resistance [132]. However, Liu et al. studied the corrosion behavior of the magnesium to steel joints produced by TIG-assisted laser process in NaCl solution. It was found that the grain refinement and iron splashes imposed by welding process were observed in the weld, which accelerated the corrosion of the magnesium alloy. Interestingly, the use of Al coating was reported to raise the lifespan of the dissimilar joints [47].
A comparison of the Mg alloys/steel joints maximum tensile shear strength produced by laser-TIG process is shown in Table 6. In hybrid laser-TIG welding, excessive vaporization of the magnesium was observed due to the penetration of the laser from upper magnesium plate and the interlayer into the bottom steel. Furthermore, the violent stirring of molten pool restricted metallurgical bonding adjacent to the steel interface, which limited the application of this welding technique. Despite the fast heating and cooling rate of the TIG-assisted laser process, the interfacial reaction was achieved through diffusion and combination of alloying elements from the BM. Based on the existing literature, the interfacial characteristics and the mechanism of wetting in Mg alloys to steel joints produced using TIG-assisted laser process with addition of interlayers were thoroughly investigated. The feasibility of using Cu, Ni, Sn, Zn, and Cu-Zn intermediate elements was also explored. The presence of interlayer was essential for successful joining Mg to steel. The selection of a suitable interlayer was essential for successful bonding. For instance, the Sn added joint shows comparatively lower value due to inhomogeneous compositions in the FZ. A comparison of the joints mechanical properties shows that excellent static strength has been achieved, even surpassing that of magnesium alloy base metal with insertion of Cu and Ni intermediate elements. The high joint shear strength obtained was associated with better wettability and deeper penetration in the weld. However, limited studies focused on corrosion behavior of the TIG-assisted laser magnesium to steel joints. Furthermore, no study has focused on the behavior of the joints under dynamic loading.
Techniques | Materials | Joint design | Transition material | Maximum tensile shear strength (MPa) | Failure mode | References |
---|---|---|---|---|---|---|
Laser-GTA | 1.7 mm AZ31B/1.2 mm 304 steel | Lap (Mg on top) | No interlayer | 90 | Interfacial | [33] |
Laser-TIG | 1.7 mm AZ31B/1.2 mm Q235 | Lap (Mg on top) | No interlayer | 120 | Interfacial | [36, 39, 96] |
Pure Cu foil (0.1 mm thick) | 170 | FZ | [38] | |||
Pure Ni foil (0.1 mm thick) | 166 | |||||
Pure Sn foil (0.1 mm thick) | 117 | |||||
Cu-Zn (H80)-0.1 mm thick | 161 | |||||
Cu-Zn (H62)-0.1 mm thick | 157 | |||||
Laser-TIG | 1.5 mm AZ31B/1.5 mm DP980 | Lap (Mg on top) | Zn coating (10 to 15 μm thick) | 68 | Interfacial | [89] |
Laser-TIG | 1.6 mm AZ31B/1.1 mm Q235 | Butt (0.2 mm offset on steel) | Cu-Zn alloy (H62) 0.1 mm thick | 203 | Weld seam | [97] |
Comparison of the magnesium alloys/steel joints maximum tensile shear strength produced by laser-TIG process.
Arc welding involves joining the materials surface permanently using power supply to obtain an electric arc between the electrode mounted in a torch and a metal. Among the arc welding processes, so far only metal inert gas welding has been used for this material combination.
Metal inert gas (MIG) welding has been widely used in automobile industries due its inherent properties, such as high efficiency, lower cost, and excellent adoptability to material geometry [133, 134]. Therefore, obtaining a reliable Mg alloy to steel joint by MIG welding is essential. However, joining magnesium to steel by MIG is rarely reported, including AZ31B/Zn-coated steel [99, 101, 102, 135], AZ31B/Q235 with Cu interlayer [72, 100] and AZ31B/Aluminized steel [102]. Generally, the addition of suitable interlayer improves the spreadability and the nucleation of magnesium on the steels.
Cold metal transfer (CMT) modified gas metal arc welding of AZ31B Mg to galvanized and bare mild steel sheets showed that welded brazed joints formed in both joints [99, 101].
A comparison of the Mg alloys/steel joints maximum tensile shear strength produced by MIG welding brazing is shown in Table 7. Generally, the investigation on the Mg alloys/steel joints produced by MIG welding is still in its infancy. Therefore, more interlayers should be tested. Moreover, the behavior of the joints under dynamic loading should be studied.
Techniques | Materials | Joint design | Transition material | Maximum tensile strength | Failure mode | References |
---|---|---|---|---|---|---|
CMT Welding | 1 mm AZ31B/Mild steel | Lap (Mg on top) | HDG Zn coating (10 μm) | 224 N/mm | Interfacial | [99, 101] |
Uncoated | 258 N/mm | Mg HAZ | ||||
Bypass current-MIG-welding | 2.5 mm AZ31B/ 2 mm Q235, with 1.6 mm AZ31 filler | Lap (Mg on top) | Zn coating | 133.02 MPa | weld metal | [135] |
MIG spot welding | 1.8 mm AZ31B/1.5 mm Q235 with 1.2 mm ER50-6 filler | Lap (Steel on top) | Pure Cu foil (0.1 mm) | 3200 N | Interfacial | [72] |
MIG spot welding | 3 mm AZ31B/3 mm Q235, 1.6 mm Mg based filler | Butt (V groove) | Uncoated | 160 MPa | Interfacial | [100] |
Pure Cu foil (0.1 mm) | 185 MPa | weld metal | ||||
CMT brazing | 2 mm AZ31/1 mm steel with 1.2 mm AZ31 filler | Lap (Mg on top) | Zn coating (10 μm) | 3100 N | Interfacial | [102] |
Zn-Fe (8 μm) | 4100 N | |||||
Uncoated | 7000 N | Weld metal | ||||
AlSi Coating (25–30 μm) | 6000 N |
Comparison of the Mg alloys/steel joints maximum tensile shear strength produced by MIG welding brazing.
As there is a desire in the aerospace, aircraft, and automotive industries to join magnesium alloys to steel in order to achieve lighter weight, versatile, and tailored properties in one composite part, and development of a welding technology for Mg alloys/steel with a strong metallurgical bond will expedite increased applications of magnesium alloys in these industries. The major challenge in welding of magnesium alloys to steel is the huge differences in physical properties and limited solubility that make the welding process difficult. Different joining processes have been used to join Mg alloys to steel sheets but metallurgical bonding can only be possible with insertion of intermediate interlayer elements or alloy or mutual diffusion of alloying elements from BM. The existence of intermetallic phases or solid solutions between Mg and the interlayer and also the interlayer and Fe is an indication that metallurgical bonding between Mg and Fe using the interlayer may be possible. Formation of thick, brittle intermetallic compounds along the interface between Mg and steel can cause significant deterioration of mechanical properties. Therefore, when choosing the interlayer and the joining process that will be used, minimization of the thickness of any brittle IMCs that might form at magnesium alloy-interlayer-steel joint interfaces and minimization of intermixing between the Mg and Fe in the liquid state are main factors that must be considered.
Solid-state bonding techniques based on FSW, USW, and diffusion and eutectic bonding have been used. Generally, the intimate contact between the dissimilar materials and the formation of IMC with insertion of the suitable interlayer played a significant role in controlling the joint performance of solid-state bonded magnesium alloys to steel.
Joining magnesium alloys to different grades of steels by fusion processes such as RSW, laser welding, and arc welding with and without insertion of interlayers were also reported. Despite the fast heating and cooling rate of the fusion process, the interfacial reaction was achieved through diffusion and combination of alloying elements from the BM. The phase formation in the magnesium-interlayer-steel alloy system and the mechanism of wetting in magnesium-interlayer-steel alloy system were extensibility investigated. The benefits of using Cu, Ni, Sn, Zn, and Cu-Zn interlayers were also explored. The addition of suitable interlayer improves the spreadability and the nucleation of magnesium on the steel substrate. Therefore, more interlayer materials that form the eutectic phase with Mg either in a pure form such as Ag and Al or as alloys such as Al-Cu and Ag-Sn should be investigated.
Currently, a great deal of research has been conducted on the interface characteristics and mechanical performance of Mg alloys to steel joints, particularly under static loading. Under optimized processing conditions, excellent static strength has been achieved, even surpassing that of Mg alloy base metal with insertion of Ag, Cu, and Ni intermediate elements. However, few experiments have been carried out on the corrosion behavior of the jointed parts and the joints performance under dynamic loading. Thus, cost-effective and reliable joining techniques for Mg/steel will still require further development. The need for the industries for more advanced materials to accommodate the huge demands for strong, rigid and light structures may be the powerful drivers for further development of the welding techniques of hybrid structures of Mg alloys to steel.
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Aydin"}]},{id:"55345",doi:"10.5772/intechopen.68883",title:"Titanium Dioxide as Food Additive",slug:"titanium-dioxide-as-food-additive",totalDownloads:2431,totalCrossrefCites:14,totalDimensionsCites:30,abstract:"Titanium dioxide is a white metal oxide used in many food categories as food additives to provide a whitening effect. If its use complies with the five specifications including synthesis pathway, crystallographic phase, purity, amount and innocuousness, all other parameters are not defined and were hardly documented. However, in the last 3 years, two studies have deeply characterized food-grade TiO2 and converged to the fact that the size distribution of food-grade TiO2 spans over the nanoparticle range (<100 nm) and the surface is not pure TiO2 but covered by phosphate and eventually silicon species or aluminium species, which modify the surface chemistry of these particles. Until now, this material was considered as safe. However, the toxicological studies later to the last re-evaluation by the European Food Safety Agency reveal some concerns due to the ability of TiO2 particles to alter the intestinal barrier. This reinforces the idea to go on reinforcing the risk assessment about food-grade TiO2.",book:{id:"6407",slug:"application-of-titanium-dioxide",title:"Application of Titanium Dioxide",fullTitle:"Application of Titanium Dioxide"},signatures:"Marie-Hélène Ropers, Hélène Terrisse, Muriel Mercier-Bonin and\nBernard Humbert",authors:[{id:"203603",title:"Dr.",name:"Marie-Hélène",middleName:null,surname:"Ropers",slug:"marie-helene-ropers",fullName:"Marie-Hélène Ropers"},{id:"206434",title:"Dr.",name:"Hélène",middleName:null,surname:"Terrisse",slug:"helene-terrisse",fullName:"Hélène Terrisse"},{id:"206435",title:"Dr.",name:"Muriel",middleName:null,surname:"Mercier-Bonin",slug:"muriel-mercier-bonin",fullName:"Muriel Mercier-Bonin"},{id:"206436",title:"Prof.",name:"Bernard",middleName:null,surname:"Humbert",slug:"bernard-humbert",fullName:"Bernard Humbert"}]},{id:"51808",doi:"10.5772/64654",title:"Plasma-Enhanced Chemical Vapor Deposition: Where we are and the Outlook for the Future",slug:"plasma-enhanced-chemical-vapor-deposition-where-we-are-and-the-outlook-for-the-future",totalDownloads:7757,totalCrossrefCites:8,totalDimensionsCites:29,abstract:"Chemical vapor deposition (CVD) is a technique for the fabrication of thin films of polymeric materials, which has successfully overcome some of the issues faced by wet chemical fabrication and other deposition methods. There are many hybrid techniques, which arise from CVD and are constantly evolving in order to modify the properties of the fabricated thin films. Amongst them, plasma enhanced chemical vapor deposition (PECVD) is a technique that can extend the applicability of the method for various precursors, reactive organic and inorganic materials as well as inert materials. Organic/inorganic monomers, which are used as precursors in the PECVD technique, undergo disintegration and radical polymerization while exposed to a high-energy plasma stream, followed by thin film deposition. In this chapter, we have provided a summary of the history, various characteristics as well as the main applications of PECVD. By demonstrating the advantages and disadvantages of PECVD, we have provided a comparison of this technique with other techniques. PECVD, like any other techniques, still suffers from some restrictions, such as selection of appropriate monomers, or suitable inlet instrument. However, the remarkable properties of this technique and variety of possible applications make it an area of interest for researchers, and offers potential for many future developments.",book:{id:"5211",slug:"chemical-vapor-deposition-recent-advances-and-applications-in-optical-solar-cells-and-solid-state-devices",title:"Chemical Vapor Deposition",fullTitle:"Chemical Vapor Deposition - Recent Advances and Applications in Optical, Solar Cells and Solid State Devices"},signatures:"Yasaman Hamedani, Prathyushakrishna Macha, Timothy J. Bunning,\nRajesh R. Naik and Milana C. Vasudev",authors:[{id:"181604",title:"Dr.",name:"Milana",middleName:null,surname:"Vasudev",slug:"milana-vasudev",fullName:"Milana Vasudev"}]},{id:"55301",doi:"10.5772/intechopen.68802",title:"Recent Overview on the Abatement of Pesticide Residues in Water by Photocatalytic Treatment Using TiO2",slug:"recent-overview-on-the-abatement-of-pesticide-residues-in-water-by-photocatalytic-treatment-using-ti",totalDownloads:1982,totalCrossrefCites:9,totalDimensionsCites:26,abstract:"The water bodies’ pollution with phytosanitary products can pose a serious threat to aquatic ecosystems and drinking water resources. The usual appearance of pesticides in surface water, waste water and groundwater has driven the search for proper methods to remove persistent pesticides. Although typical biological treatments of water offer some advantages such as low cost and operability, many investigations referring to the removal of pesticides have suggested that in many cases they have low effectiveness due to the limited biodegradability of many agrochemicals. In recent years, research for new techniques for water detoxification to avoid these disadvantages has led to processes that involve light, which are called advanced oxidation processes (AOPs). Among the different semiconductor (SC) materials tested as potential photocatalysts, titanium dioxide (TiO2) is the most popular because of its photochemical stability, commercial availability, non-toxic nature and low cost, high photoactivity, ease of preparation in the laboratory, possibility of doping with metals and non-metals and coating on solid support. Thus, in the present review, we provide an overview of the recent research being developed to photodegrade pesticide residues in water using TiO2 as photocatalyst.",book:{id:"6407",slug:"application-of-titanium-dioxide",title:"Application of Titanium Dioxide",fullTitle:"Application of Titanium Dioxide"},signatures:"Nuria Vela, Gabriel Pérez-Lucas, José Fenoll and Simón Navarro",authors:[{id:"202983",title:"Dr.",name:"Simón",middleName:null,surname:"Navarro",slug:"simon-navarro",fullName:"Simón Navarro"},{id:"202988",title:"Dr.",name:"Nuria",middleName:null,surname:"Vela",slug:"nuria-vela",fullName:"Nuria Vela"},{id:"202989",title:"Dr.",name:"José",middleName:null,surname:"Fenoll",slug:"jose-fenoll",fullName:"José Fenoll"},{id:"206059",title:"Dr.",name:"Gabriel",middleName:null,surname:"Pérez-Lucas",slug:"gabriel-perez-lucas",fullName:"Gabriel Pérez-Lucas"}]}],mostDownloadedChaptersLast30Days:[{id:"55440",title:"Solubility Products and Solubility Concepts",slug:"solubility-products-and-solubility-concepts",totalDownloads:3051,totalCrossrefCites:6,totalDimensionsCites:7,abstract:"The chapter refers to a general concept of solubility product Ksp of sparingly soluble hydroxides and different salts and calculation of solubility of some hydroxides, oxides, and different salts in aqueous media. A (criticized) conventional approach, based on stoichiometry of a reaction notation and the solubility product of a precipitate, is compared with the unconventional/correct approach based on charge and concentration balances and a detailed physicochemical knowledge on the system considered, and calculations realized according to generalized approach to electrolytic systems (GATES) principles. An indisputable advantage of the latter approach is proved in simulation of static or dynamic, two-phase nonredox or redox systems.",book:{id:"5891",slug:"descriptive-inorganic-chemistry-researches-of-metal-compounds",title:"Descriptive Inorganic Chemistry Researches of Metal Compounds",fullTitle:"Descriptive Inorganic Chemistry Researches of Metal Compounds"},signatures:"Anna Maria Michałowska-Kaczmarczyk, Aneta Spórna-Kucab and\nTadeusz Michałowski",authors:[{id:"35273",title:"Prof.",name:"Tadeusz",middleName:null,surname:"Michalowski",slug:"tadeusz-michalowski",fullName:"Tadeusz Michalowski"},{id:"203867",title:"Dr.",name:"Anna Maria",middleName:null,surname:"Michałowska-Kaczmarczyk",slug:"anna-maria-michalowska-kaczmarczyk",fullName:"Anna Maria Michałowska-Kaczmarczyk"},{id:"203868",title:"Dr.",name:"Aneta",middleName:null,surname:"Spórna-Kucab",slug:"aneta-sporna-kucab",fullName:"Aneta Spórna-Kucab"}]},{id:"56162",title:"Phosphoric Acid Industry: Problems and Solutions",slug:"phosphoric-acid-industry-problems-and-solutions",totalDownloads:5234,totalCrossrefCites:2,totalDimensionsCites:9,abstract:"Phosphoric acid (PA) is an important industrial chemical used as an intermediate in the fertilizer industry, for metal surface treatment in the metallurgical industry and as an additive in the food industry. The PA industry is spread out worldwide in Europe, Asia and America, including countries that operate phosphate rock (PR) mines and produce PA, phosphatic fertilizers and phosphate-based products.",book:{id:"5595",slug:"phosphoric-acid-industry-problems-and-solutions",title:"Phosphoric Acid Industry",fullTitle:"Phosphoric Acid Industry - Problems and Solutions"},signatures:"Benjamín Valdez Salas, Michael Schorr Wiener and Juan Ricardo\nSalinas Martinez",authors:[{id:"16436",title:"Dr.",name:"Michael",middleName:null,surname:"Schorr",slug:"michael-schorr",fullName:"Michael Schorr"}]},{id:"62941",title:"Inorganic Coordination Chemistry: Where We Stand in Cancer Treatment?",slug:"inorganic-coordination-chemistry-where-we-stand-in-cancer-treatment-",totalDownloads:2113,totalCrossrefCites:5,totalDimensionsCites:10,abstract:"Metals have unique characteristics such as variable coordination modes, redox activity, and reactivity being indispensable for several biochemical processes in cells. Due to their reactivity, their concentration is tightly regulated inside the cells, and abnormal concentrations are associated with many disorders, such as cancer. As such metal complexes turned out to be very attractive as potential anticancer agents. The discovery of cisplatin was a crucial moment, which prompted the interest in Pt(II) and other metal complexes as potential anticancer agents. This chapter highlights the state of the art on metal complexes in cancer therapy, highlighting their uptake mechanisms, biological targets, toxicity, and drug resistance. Finally, based on the importance of selective target of cancer cells, drug delivery systems will also be discussed.",book:{id:"7549",slug:"basic-concepts-viewed-from-frontier-in-inorganic-coordination-chemistry",title:"Basic Concepts Viewed from Frontier in Inorganic Coordination Chemistry",fullTitle:"Basic Concepts Viewed from Frontier in Inorganic Coordination Chemistry"},signatures:"Pedro Pedrosa, Andreia Carvalho, Pedro V. Baptista and Alexandra R. Fernandes",authors:[{id:"253664",title:"Prof.",name:"Alexandra R",middleName:null,surname:"Fernandes",slug:"alexandra-r-fernandes",fullName:"Alexandra R Fernandes"}]},{id:"57464",title:"General Aspects of the Cobalt Chemistry",slug:"general-aspects-of-the-cobalt-chemistry",totalDownloads:2271,totalCrossrefCites:1,totalDimensionsCites:2,abstract:"This chapter aims to collect and summarize the chemical properties of cobalt and some new cobalt compounds. It deals with the progress of cobalt chemistry. Cobalt has been substantial in both chemical reactions and within many compounds. Some of them are heterocyclic reactions, cobalt-based catalyst and cobalamin. Also, it discusses variety of applications of cobalt in a wide range of areas and toxicity of cobalt. The studies carried out in this area so far have enabled and will be continued to be responsible for producing unknown and difficult reactions. This survey of the recent literature illustrates the fact that many different approaches on cobalt and new cobalt compounds are being used in many different areas.",book:{id:"6133",slug:"cobalt",title:"Cobalt",fullTitle:"Cobalt"},signatures:"Yasemin Yildiz",authors:[{id:"208129",title:"Dr.",name:"Yasemin",middleName:null,surname:"Yıldız",slug:"yasemin-yildiz",fullName:"Yasemin Yıldız"}]},{id:"55301",title:"Recent Overview on the Abatement of Pesticide Residues in Water by Photocatalytic Treatment Using TiO2",slug:"recent-overview-on-the-abatement-of-pesticide-residues-in-water-by-photocatalytic-treatment-using-ti",totalDownloads:1982,totalCrossrefCites:9,totalDimensionsCites:26,abstract:"The water bodies’ pollution with phytosanitary products can pose a serious threat to aquatic ecosystems and drinking water resources. The usual appearance of pesticides in surface water, waste water and groundwater has driven the search for proper methods to remove persistent pesticides. 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