2005-High power high efficiency AlGaN-GaN HEMT technology for wireless base station applications

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维沙亚高抗性 高压金属玻璃带领导电阻说明书

维沙亚高抗性 高压金属玻璃带领导电阻说明书

VR25000003303JA 100VR37000003904JA100VR25000008204JA100VR37000002005FA100VR37000002204FA100VR25, VR37, VR68Vishay BCcomponentsHigh Ohmic / High Voltage Metal Glaze Leaded ResistorsDESIGN SUPPORT TOOLSA metal glazed film is deposited on a high grade ceramic body. After a helical groove has been cut in the resistive layer, tinned electrolytic copper wires are welded to the end-caps. The resistors are coated with a light blue lacquer which provides electrical, mechanical, and climatic protection.FEATURES•UL Approved (UL1676, file no: E171160)•Meet the safety requirements of:-IEC 60065-DIN EN 60065-VDE 0860-CQC (China)•AEC-Q200 qualified (VR25, VR37)•High pulse loading capability (maximum 10 kV)•Radial version available for VR25•Material categorization: for definitions of compliance please see /doc?99912APPLICATIONS•Where high resistance, high stability, and high reliability at high voltage are required •High humidity environment •White goods •Power supplies •Automotive electronicsNote(1)Ohmic values (other than resistance range) are available on requestTECHNICAL SPECIFICATIONSDESCRIPTION VR25VR37VR68Imperial size 020*********Resistance range (1)100 k Ω to 22 M Ω100 k Ω to 33 M Ω100 k Ω to 68 M ΩResistance tolerance ± 10 %; ± 5 %; ± 1 %Temperature coefficient ≤ ± 200 ppm/KRated dissipation, P 700.25 W 0.5 W 1.0 W Operating voltage, U max. AC/DC 1600 V 3500 V 10 000 V Operating temperature range -55 °C to +155 °CPeak permissible film temperature 155 °C Thermal resistance (R th )140 K/W 120 K/W70 K/W Insulation voltage:1 min.; U ins700 V Maximum noise (white noise)5 μV/V 2.5 μV/V 2.5 μV/V Max. resistance change atrated dissipation for resistance range, |∆R /R | max., after 1000 h1.5 %1.5 %1.5 %SAFETY REQUIREMENTS AND QUALIFICATIONSDESCRIPTIONVR25, VR37VR37VR68Safety requirements / qualifications AEC-Q200UL1676 qualification (file no: E171160)for ohmic range 510 k Ω to 11 M Ω;DIN EN 60065 (VDE 0860): 2015; clause 14.2 a);EN 60065: 2014IEC 60065: clause 14.2 a)CQCVR25, VR37, VR68Vishay BCcomponentsNote(1)See table “Temperature Coefficient and Resistance Range” for selecting correct ohmic value - tolerance combinationTEMPERATURE COEFFICIENT AND RESISTANCE RANGETYPE TCRTOLERANCERESISTANCE E-SERIES VR25≤ ± 200 ppm/K± 1 %100 k Ω to 15 M ΩE24; E96± 5 %100 k Ω to 22 M ΩE24; E96± 10 %15 M Ω to 22 M ΩE24VR37± 1 %100 k Ω to 33 M ΩE24; E96± 5 %100 k Ω to 33 M ΩE24VR68± 1 %100 k Ω to 68 M ΩE24; E96± 5 %100 k Ω to 68 M ΩE24PART NUMBER AND PRODUCT DESCRIPTIONPART NUMBER: VR25000001003FA100TYPE / SIZE VARIANT TCR RESISTANCE TOLERANCE (1)PACKAGINGSPECIAL VR25000 = VR25VR37000 = VR37VR68000 = VR680 = neutral0 = standard3 digit value 1 digit multiplier MULTIPLIER 0 = *1001 = *1012 = *1023 = *1034 = *1045 = *1056 = *106F = ± 1 %J = ± 5 %K = ± 10 %A1AC A5RD R5N400 = standardPRODUCT DESCRIPTION: VR25 1 % A1 100KVR25 1 %A1100K TYPE / SIZETOLERANCE PACKAGINGRESISTANCE VR25VR37VR68± 1 %± 5 %± 10 %A1AC A5RD R5N4100K = 100 k Ω15M = 15 M ΩPACKAGINGTYPECODE QUANTITY PACKAGING STYLEWIDTH PITCH DIMENSIONS VR25A11000Taped according to IEC 60286-1 fan-folded in a box 53 mm 5 mm 75 mm x 31 mm x 260 mm A5500053 mm 5 mm 76 mm x 105 mm x 265 mm N44000Taped according to IEC 60286-2 fan-folded in a box-12.7 mm 48 mm x 253 mm x 330 mm R55000Taped according to IEC 60286-1 on a reel 53 mm 5 mm 93 mm x 300 mm x 298 mm VR37A11000Taped according to IEC 60286-1 fan-folded in a box53 mm 5 mm 72 mm x 60 mm x 258 mm R55000Taped according to IEC 60286-1 on a reel 53 mm 5 mm 90 mm x 375 mm x 375 mm VR68AC 500Taped according to IEC 60286-1 fan-folded in a box66 mm 10 mm 82 mm x 111 mm x 256 mm RD750Taped according to IEC 60286-1 on a reel66 mm10 mm105 mm x 315 mm x 305 mmV R 5000001003F A 1002VR25, VR37, VR68 Vishay BCcomponentsDESCRIPTIONProduction is strictly controlled and follows an extensive set of instructions established for reproducibility. A homogeneous film of metal alloy is deposited on a high grade ceramic body and conditioned to achieve the desired temperature coefficient. Plated steel termination caps are firmly pressed on the metalized rods. Mostly, a special laser is used to achieve the target value by smoothly cutting a helical groove in the resistive layer without damaging the ceramics. Connecting wires of electrolytic copper plated with 100 % pure tin are welded to the termination caps. The resistor elements are covered by a light blue protective coating designed for electrical, mechanical, and climatic protection. Four or five color code rings designate the resistance value and tolerance in accordance with IEC 60062.Yellow and gray are used instead of gold and silver because metal particles in the lacquer could affect high-voltage properties.The result of the determined production is verified by an extensive testing procedure performed on 100 % of the individual resistors. Only accepted products are stuck directly on the adhesive tapes in accordance with IEC 60286-1 or for the radial versions in accordance to IEC 60286-2.MATERIALSVishay acknowledges the following systems for the regulation of hazardous substances:•IEC 62474, Material Declaration for Products of and for the Electrotechnical Industry, with the list of declarable substances given therein (1)•The G lobal Automotive Declarable Substance List (GADSL) (2)•The REACH regulation (1907/2006/EC) and the related list of substances with very high concern (SVHC) (3) for its supply chainThe products do not contain any of the banned substances as per IEC 62474, G ADSL, or the SVHC list, see /how/leadfree.Hence the products fully comply with the following directives:•2000/53/EC End-of-Life Vehicle Directive (ELV) and Annex II (ELV II)•2011/65/EU Restriction of the Use of Hazardous Substances Directive (RoHS) with amendment 2015/863/EU•2012/19/EU Waste Electrical and Electronic Equipment Directive (WEEE)Vishay pursues the elimination of conflict minerals from its supply chain, see the Conflict Minerals Policy at /doc?49037.ASSEMBLYThe resistors are suitable for processing on automatic insertion equipment and cutting and bending machines. Excellent solderability is proven, even after extended storage. They are suitable for automatic soldering using wave or dipping.The resistors are completely lead (Pb)-free, the pure tin plating provides compatibility with lead (Pb)-free and lead-containing soldering processes. The immunity of the plating against tin whisker growth, in compliance with IEC 60068-2-82, has been proven under extensive testing. The encapsulant is resistant to cleaning solvent specified in IEC 60115-1. The suitability of conformal coatings, if applied, shall be qualified by appropriate means to ensure the long-term stability of the whole system.APPROVALSThese resistors meet the safety requirements of:•UL1676 (510 kΩ to 11 MΩ); file no: E171160•IEC 60065, clause 14.2 a)•DIN EN 60065, clause 14.2 a)•VDE 0860, clause 14.2 a)•CQC, ChinaRELATED PRODUCTSFor a correlated range of Metal Film Resistors see the datasheet:“High Ohmic / High Voltage Metal Film Leaded Resistors”, /doc?30260For product that offers high power dissipation and metal oxide film technology see the datasheet:“High Power Metal Oxide Leaded Resistors”,/doc?20128Notes(1)The IEC 62474 list of declarable substances is maintained in a dedicated database, which is available at http://std.iec.ch/iec62474(2)The G lobal Automotive Declarable Substance List (G ADSL) is maintained by the American Chemistry Council, and available atVR25, VR37, VR68Vishay BCcomponentsFUNCTIONAL PERFORMANCEDeratingHot-Spot Temperature Rise ( T) as a Function of Dissipated PowerVR25VR37VR25, VR37, VR68 Vishay BCcomponentsMaximum allowed peak pulse voltage in accordance with IEC 60065, 14.2 a);50 discharges from a 1nF capacitor charged to Ûmax.; 12 discharges/min (drift ∆R/R≤ 2 %)VR25VR37VR25, VR37, VR68 Vishay BCcomponentsTemperature Rise ( T) at the Lead End (Soldering Point) as a Function of Dissipated Power at Various Lead Lengths after MountingVR25VR37VR25, VR37, VR68Vishay BCcomponentsTESTS PROCEDURES AND REQUIREMENTSAll tests are carried out in accordance with the following specifications:•IEC 60115-1, generic specification (includes tests)The test and requirements table contains only the most important tests. For the full test schedule refer to the documents listed above.The tests are carried out with reference to IEC 60115-1, in accordance with IEC 60068-2-xx test method and under standard atmospheric conditions in accordance with IEC 60068-1, 5.3.A climatic category 55 / 155 / 56 is applied, defined by the lower category temperature (LCT = -55 °C), the upper category temperature (UCT = 155 °C), and the duration of exposure in the damp heat, steady state test (56 days).Unless otherwise specified the following values apply:•Temperature: 15 °C to 35 °C •Relative humidity: 45 % to 75 %•Air pressure: 86 kPa to 106 kPa (860 mbar to 1060 mbar).For performing some of the tests, the components are mounted on a test board in accordance with IEC 60115-1, 4.31.In test procedures and requirements table, only the tests and requirements are listed with reference to the relevant clauses of IEC 60115-1 and IEC 60068-2-xx test methods. A short description of the test procedure is also given.TESTS PROCEDURES AND REQUIREMENTSIEC 60115-1 CLAUSE IEC 60068-2TEST METHOD TESTPROCEDUREREQUIREMENTS PERMISSIBLE CHANGE(∆R max.)4.6.1.1Insulation resistanceU max. DC = 500 V during 1 min; V-block methodR ins min.: 10 000 M Ω4.7Voltage proof U RMS = U ins ; 60 sNo breakdown or flashover4.8Temperature coefficientAt (20 / -55 / 20) °C and (20 / 155 / 20) °C≤ ± 200 ppm/K 4.12NoiseIEC 60195VR25: max. 5 μV/V VR37: max. 2.5 μV/V VR68: max. 2.5 μV/V 4.13Short time overload Room temperature; 2.5 x ;(voltage not more than 2 x limiting voltage);10 cycles; 5 s ON and 45 s OFF∆R max.: ± 2 % R 4.1621 (Ua1)21 (Ub)21 (Uc)Robustness of terminationsTensile, bending, and torsionNo damage ∆R max.: ± 0.5 % R4.1720 (Ta)Solderability+235 °C; 2 s; solder bath method; SnPb40+245 °C; 3 s; solder bath method; SnAg3Cu0.5(before aging)Good tinning (≥ 95 % covered);no damage+235 °C; 2 s; solder bath method; SnPb40+245 °C; 3 s; solder bath method; SnAg3Cu0.5(after aging)Good tinning (≥ 95 % covered);no damage4.1820 (Tb)Resistance to soldering heat Unmounted components (260 ± 5) °C; (10 ± 1) s∆R max.: ± 0.5 % R 4.1914 (Na)Rapid change of temperature30 min at -55 °C and 30 min at +155 °C;5 cycles ∆R max.: ± 0.5 % R 4.2029 (Eb)Bump 3 x 1500 bumps in 3 directions; 40 g No damage ∆R max.: ± 0.5 % R 4.226 (Fc)Vibration 10 sweep cycles per direction;10 Hz to 2000 Hz;1.5 mm or 200 m/s 2No damage ∆R max.: ± 0.5 % R4.23Climatic sequence:R ins min.: 1 G Ω∆R max.: ± 1.5 % R4.23.2 2 (Bb)Dry heat 16 h; 155 °C 4.23.330 (Db)Damp heat cyclic 24 h; 25 °C to 55 °C;90 % to 100 % RH4.23.4 1 (Ab)Cold 2 h; -55 °C 4.23.513 (M)Low air pressure 2 h; 8.5 kPa;15 °C to 35 °C4.23.630 (Db)Damp heat remaining cyclic5 days; 55 °C;95 % to 100 % RH; 5 cycles P 70 x RVR25, VR37, VR68Vishay BCcomponentsDIMENSIONSVR25 WITH RADIAL TAPINGLead Spacing (F = 4.8 mm), Size 02074.2478 (Cab)Damp heat(steady state)56 days; 40 °C;90 % to 95 % RH; loaded with 0.01 P 70(steps: 0 V to 100 V)∆R max.: ± 1.5 % R 4.25.1Endurance (at 70 °C)1000 h; loaded with P 70 or U max.;1.5 h ON and 0.5 h OFF ∆R max.: ± 1.5 % R 4.26Active flammability “cheese-cloth test”Steps of:5 / 10 / 16 / 25 / 40 x P 70 duration 5 minVR25: no flaming of gauze cylinder VR68: no flaming of gauze cylinder 4.35Passive flammability “needle-flame test”Application of test flame for 20 sNo ignition of product;no ignition of under-layer;burning time less than 30 sDIMENSIONS - Leaded resistor types, mass, and relevant physical dimensionsTYPE Ø D max. (mm)L 1 max. (mm)L 2 max. (mm)Ø d (mm)MASS (mg)VR25 2.5 6.57.50.58 ± 0.05212VR37 4.09.010.00.70 ± 0.03457VR686.818.019.00.78 ± 0.051690TESTS PROCEDURES AND REQUIREMENTSIEC 60115-1 CLAUSE IEC 60068-2TEST METHOD TEST PROCEDUREREQUIREMENTS PERMISSIBLE CHANGE(∆R max.)L dDIMENSIONS in millimetersPitch of components P 12.7 ± 1.0Lead spacing F 4.8 + 0.7 / - 0.0Width of carrier tape W 18.0 ± 0.5Body to hole centerH 19.5 ± 1.0Height for cutting (max.)L 11Height for bending H 016.5 ± 0.5Component height (max.)H 129VR25, VR37, VR68 Vishay BCcomponentsHISTORICAL 12NC INFORMATION•The resistors have a 12-digit numeric code starting with -2322 241 refers to VR25-2322 242 refers to VR37-2322 244 refers to VR68•The subsequent first digit for 1 % tolerance products (E24 and E96 series) or 2 digits for 5 % (E24 series) and 10 % (E12 series) indicate the resistor type and packing•The remaining digits indicate the resistance value:-The first 3 digits for 1 % or 2 digits for 5 % and 10 % tolerance products indicate the resistance value-The last digit indicates the resistance decadeLast Digit of 12NC Indicating Resistance DecadeHistorical 12NC Example•The 12NC for a VR25, resistor value 7.5 MΩ, 5 % tolerance, supplied on a bandoleer of 1000 units in ammopack, is: 2322 241 13755.•The 12NC for a VR37, resistor value 7.5 MΩ, 5 % tolerance, supplied on a bandoleer of 1000 units in ammopack, is: 2322 242 13755.•The 12NC for a VR68, resistor value 7.5 MΩ, 5 % tolerance, supplied on a bandoleer of 500 units in ammopack, is: 2322 244 13755.RESISTANCE DECADE LAST DIGIT100 kΩ to 976 kΩ41 MΩ to 9.76 MΩ5≥ 10 MΩ612NC CODING FOR VR25, VR37, VR68 - Resistor type and packagingTYPE TOLERANCE(%)VR25 CODING STARTS WITH 2322 241 .....VR37 CODING STARTS WITH 2322 242 .....VR68 CODING STARTS WITH 2322 244 .....BANDOLIER IN AMMOPACK BANDOLIER ON REEL RADIAL TAPED STRAIGHT LEADS4000 UNITS52 mm52 mm66.7 mm52 mm66.7 mm1000 UNITS5000 UNITS500 UNITS5000 UNITS750 UNITSVR25± 10....8....7....- 6....-± 536...13...53...-23...-± 1038...12...52...-22...-VR37± 1-8....-- 6....-± 5-13...--23...-VR68± 1---8....- 6....± 5---13...-23...Legal Disclaimer Notice VishayDisclaimerALL PRODUCT, PRODUCT SPECIFICATIONS AND DATA ARE SUBJECT TO CHANGE WITHOUT NOTICE TO IMPROV E RELIABILITY, FUNCTION OR DESIGN OR OTHERWISE.V ishay Intertechnology, Inc., its affiliates, agents, and employees, and all persons acting on its or their behalf (collectively,“Vishay”), disclaim any and all liability for any errors, inaccuracies or incompleteness contained in any datasheet or in any other disclosure relating to any product.Vishay makes no warranty, representation or guarantee regarding the suitability of the products for any particular purpose or the continuing production of any product. To the maximum extent permitted by applicable law, Vishay disclaims (i) any and all liability arising out of the application or use of any product, (ii) any and all liability, including without limitation special, consequential or incidental damages, and (iii) any and all implied warranties, including warranties of fitness for particular purpose, non-infringement and merchantability.Statements regarding the suitability of products for certain types of applications are based on Vishay's knowledge of typical requirements that are often placed on Vishay products in generic applications. Such statements are not binding statements about the suitability of products for a particular application. It is the customer's responsibility to validate that a particular product with the properties described in the product specification is suitable for use in a particular application. Parameters provided in datasheets and / or specifications may vary in different applications and performance may vary over time. All operating parameters, including typical parameters, must be validated for each customer application by the customer's technical experts. Product specifications do not expand or otherwise modify Vishay's terms and conditions of purchase, including but not limited to the warranty expressed therein.Hyperlinks included in this datasheet may direct users to third-party websites. These links are provided as a convenience and for informational purposes only. Inclusion of these hyperlinks does not constitute an endorsement or an approval by Vishay of any of the products, services or opinions of the corporation, organization or individual associated with the third-party website. Vishay disclaims any and all liability and bears no responsibility for the accuracy, legality or content of the third-party website or for that of subsequent links.Except as expressly indicated in writing, Vishay products are not designed for use in medical, life-saving, or life-sustaining applications or for any other application in which the failure of the Vishay product could result in personal injury or death. Customers using or selling Vishay products not expressly indicated for use in such applications do so at their own risk. Please contact authorized Vishay personnel to obtain written terms and conditions regarding products designed for such applications. No license, express or implied, by estoppel or otherwise, to any intellectual property rights is granted by this document or by any conduct of Vishay. Product names and markings noted herein may be trademarks of their respective owners.© 2022 VISHAY INTERTECHNOLOGY, INC. ALL RIGHTS RESERVEDRevision: 01-Jan-20221Document Number: 91000VR68000001003JA C00VR68000001504JA C00VR25000003303JA 100VR37000003904JA100VR25000008204JA100VR37000002005FA100VR37000002204FA100。

SGM2005资料

SGM2005资料

SGM2005Low Power, Low Dropout, 150mA, RF - Linear RegulatorsShengbang Microelectronics Co, Ltd Tel: 86/451/84348461 REV . BSGM20052ORDERING INFORMATIONMODELV OUT (V)PIN- PACKAGESPECIFIED TEMPERATURERANGEORDERING NUMBER PACKAGE MARKINGPACKAGE OPTIONSGM2005-1.8 1.8V DFN-6 - 40°C to +85°C SGM2005-1.8YD6/TR Y518 Tape and Reel, 3000 SGM2005-2.5 2.5V DFN-6 - 40°C to +85°C SGM2005-2.5YD6/TR Y525 Tape and Reel, 3000 SGM2005-2.8 2.8V DFN-6 - 40°C to +85°C SGM2005-2.8YD6/TR Y528 Tape and Reel, 3000 SGM2005-3.0 3.0V DFN-6 - 40°C to +85°C SGM2005-3.0YD6/TR Y530 Tape and Reel, 3000 SGM2005-3.3 3.3VDFN-6- 40°C to +85°CSGM2005-3.3YD6/TRY533Tape and Reel, 3000ABSOLUTE MAXIMUM RATINGSIN to GND.....................................................................- 0.3V to +6V Output Short-Circuit Duration ...........................................Infinite EN to GND...................................................................- 0.3V to +6V OUT, BP to GND............................................- 0.3V to (V IN + 0.3V) Power Dissipation, PD @ T A = 25°C DFN-6 ................................................................................... 300mW Package Thermal Resistance DFN-6,θJA ...........................................................................200℃/W Operating Temperature Range..............................- 40°C to +85°C Junction Temperature...........................................................+150°C Storage Temperature.............................................- 65°C to +150°C Lead Temperature (soldering, 10s).....................................+260°C ESD Rating..................................................................................4 kVStresses beyond those listed under “Absolute Maximum Ratings” may cause permanent damage to the device. These are stress ratings only, and functional operation of the device at these or any other conditions beyond those indicated in the operational sections of the specifications is not implied. Exposure to absolute maximum rating conditions for extended periods may affect device reliability.TYPICAL OPERATION CIRCUITELECTRICAL CHARACTERISTICS(V IN = V OUT (NOMINAL) + 0.5V (1), T A = - 40°C to +85°C, unless otherwise noted. Typical values are at T A = + 25°C.)PARAMETER SYMBOL CONDITIONS MIN TYP MAX UNITSInput VoltageV IN 2.5 5.5 V Output Voltage Accuracy (1) I OUT =1mA to150mA, T A = +25°CV OUT + 0.5V≤V IN ≤ 5.5V -2.7 +2.7 % Maximum Output Current150 mA Current Limit I LIM 160 600mA No load, EN = 2V77 145 Ground Pin Current I Q I OUT = 150mA, EN = 2V 150 µA I OUT = 1mA 1 Dropout Voltage (2) I OUT = 150mA150190mVLine Regulation (1) ΔV LNR V IN = 2.5V or (V OUT + 0.5V) to 5.5V, I OUT = 1mA0.03 0.15 %/V Load Regulation ΔV LDRI OUT = 0.1mA to 150mA, C OUT = 1µF0.00080.002%/mAOutput Voltage Noise e nf = 10Hz to 100KHz, C BP = 0.01µF, C OUT = 10µF30 µV RMS f = 100Hz, 78 dB Power Supply Rejection Rate PSRRC BP = 0.1µF, I LOAD = 50mA, C OUT = 1µFf = 1KHz, 73 dBSHUTDOWN V IH 2.0EN Input Threshold V IL V IN = 2.5V to 5.5V 0.4 VT A = +25°C 0.01 1 EN Input Bias Current I B(SHDN) EN = 0V and EN = 5.5V T A = +85°C 0.01 µA T A = +25°C 0.01 1 Shutdown Supply Current I Q(SHDN)EN = 0.4V T A = +85°C 0.01µA Shutdown Exit Delay (3)C BP = 0.01µF C OUT = 1µF, No loadT A = +25°C30µsTHERMAL PROTECTION Thermal Shutdown Temperature T SHDN 160 ℃ Thermal Shutdown HysteresisΔT SHDN15℃Specifications subject to change without notice.Note 1: V IN = V OUT(NOMINAL) + 0.5V or 2.5V, whichever is greater.Note 2: The dropout voltage is defined as V IN - V OUT , when V OUT is 100mV below the value of V OUT for V IN = V OUT + 0.5V. (Only applicable for V OUT = +2.5V to +3.3V.)Note 3: Time needed for V OUT to reach 95% of final value.TYPICAL OPERATING CHARACTERISTICSV IN = V OUT(NOMINAL) + 0.5V or 2.5V (whichever is greater), C IN = 1µF, C OUT = 1µF, C BP= 0.01µF, T A = +25℃, unless otherwise noted.TYPICAL OPERATING CHARACTERISTICSV IN = V OUT(NOMINAL) + 0.5V or 2.5V (whichever is greater), C IN = 1µF, C OUT = 1µF, C BP= 0.01µF, T A = +25℃, unless otherwise noted.TYPICAL OPERATING CHARACTERISTICSV IN = V OUT(NOMINAL) + 0.5V or 2.5V (whichever is greater), C IN = 1µF, C OUT = 1µF, C BP= 0.01µF, T A = +25℃, unless otherwise noted.TYPICAL OPERATING CHARACTERISTICSV IN = V OUT(NOMINAL) + 0.5V or 2.5V (whichever is greater), C IN = 1µF, C OUT = 1µF, C BP= 0.01µF, T A = +25℃, unless otherwise noted.Application NotesWhen LDO is used in handheld products, Attention must be paid to voltage spike which would damage SGM2005. In such applications, voltage spike will be generated at changer interface and V BUS pin of USB interface when changer adapters and USB equipments are hot-inserted. Besides this, handheld products will be tested on the production line on the condition of no battery. Test Engineer will apply power from the connector pin which connects with positive pole of the battery. When external power supply is turned on suddenly, the voltage spike will be generated at the battery connector. The voltage spike will be very high, it always exceeds the absolute maximum input voltage (6.0V) of LDO. In order to get robust design. Design Engineer needs to clear up this voltage spike. Zener diode is a cheap and effective solution to eliminate such voltage spike. For example, BZM55B5V6 is a 5.6V small package Zener diode which can be used to remove voltage spike in cell phone design. The schematic is shown in below:PACKAGE OUTLINE DIMENSIONS DFN-6NOTES:1.All dimensions are in millimeters.REVISION HISTORYLocation Page03/07— Data Sheet changed from REV. A to REV. BChanged to TYPICAL OPERATING CHARACTERISTICS . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 6Shengbang Microelectronics Co, LtdUnit 3, ChuangYe PlazaNo.5, TaiHu Northern Street, YingBin Road Centralized Industrial ParkHarbin Development ZoneHarbin,150078HeiLongJiangChinaP.R.Tel.: 86-451-84348461Fax: 86-451-84308461。

南大宽禁带半导体实验室

南大宽禁带半导体实验室

禁带半导体紫外探测器紫外探测技术在国防预警与跟踪、电力工业、环境监测及生命科学领域具有重要的应用,其核心器件是高性能的紫外光电探测器。

基于半导体材料的固态紫外探测器件具有体重小、功耗低、量子效率高、和便于集成等系列优势。

以碳化硅(SiC)和III族氮化物为代表的宽禁带半导体是近年来国内外重点研究和发展的新型第三代半导体材料,具有禁带宽度大、导热性能好、电子饱和漂移速度高以及化学稳定性优等特点,用于制备紫外波段的光探测器件具有显著的材料性能优势。

我们实验室在宽禁带半导体紫外探测器领域具有较强的实力。

率先在国内实现4H-SiC基紫外雪崩单光子探测器;分别研制成功高增益同质外延GaN基紫外雪崩光电探测器、国际上领先的高增益AlGaN基日盲雪崩光电探测器、具有极低暗电流的AlGaN基MSM日盲深紫外探测器、高量子效率AlGaN基PIN日盲深紫外探测器、以及现有芯片面积最大的AlGaN基日盲深紫外探测器,相关结果多次获得国际主流媒体的跟踪报导。

目前,我们的工作重点是研制高灵敏度宽禁带半导体紫外探测器,包括:紫外单光子探测器件结构设计和物理分析,紫外单光子探测线阵和日盲紫外探测阵列制备。

宽禁带半导体功率电子器件针对未来高效电力管理系统、电动汽车和广泛军事应用大容量化、高密度化和高频率化的要求,将宽禁带半导体材料应用于高档次功率电子器件可以有效解决当今功率电子器件发展所面临的“硅极限”(silicon limit)问题,将大幅度降低电能转换过程中的无益损耗,在各领域创造可观的节能空间。

宽禁带Ⅲ族氮化物半导体具有强击穿电场、高饱和漂移速度、高热导率和良好化学稳定性等系列材料性能优势,是制备新一代功率电子器件的理想材料。

这一研究方向近年来成为国际上继GaN基发光二极管和微波功率器件之后的新兴研究热点。

我们小组在这一研究领域具有较好的基础,已经研制成功AlGaN/GaN平面功率二极管,其击穿电压大于1100V,功率优值系数高达280MW/cm2。

MMIC功率合成技术发展动态

MMIC功率合成技术发展动态

国内外研究现状1、国内研究现状国内关于GaN微波功率合成技术的研究起步比较晚,中电集团13所,552005年,13所冯震等人制备了以蓝宝石为衬底的GaN基HEMT器件,饱和电流为890mA,最大跨导值为227ms,在频率为8GHz时连续波输出功率最大为4W,增益大于4dB,PAE为48%[1]。

2007年,中科院微电子所报道了一种基于AlGaN/GaN HEMT的功率合成技术的混合集成放大器电路。

该电路包含4个10x120μm的HEMT晶体管以及一个Wilkinson功率合成器和分配器。

在偏置条件为V DS=40V,I DS=0.9A时,输出连续波饱和功率在5.4GHz达到41.4dBm,最大的PAE为32.54%,并且功率合成效率达到69%[2]。

2007年55所的王帅等报道了研制的lmm栅宽的AlGaN/GaN HEMT内匹配微波功率管,在32V漏偏压下在7.5-9.5GHz频率范围内输出功率大于5W,功率附加效率典型值为30%,功率增益大于6dB,带内增益平坦度为±0.4dB,带内最大输出功率为6W[3]。

2008年,中科院微电子所的曾轩等人采用内匹配功率合成技术,设计了基于AlGaN/GaN HEMT的X波段内匹配功率合成放大器,偏置条件为V DS=30V,I DS=700mA时,在8GHz测出连续波,饱和输出功率达到P sat=40dBm(10W),最大PAE=37.44%,线性增益为9dB[4]。

2009年,中电13所的顾卫东等人利用MOCVD技术研制了国产SiC衬底的GaN HEMT外延材料,方块电阻小于260μm/□,迁移率最大值达到2 130cm2/v.s,方块电阻和迁移率不均匀性小于3%,采用新的器件栅结构和高应力SiN钝化技术,降低了大栅宽器件栅泄漏电流,提高了工作电压。

研制的总栅宽为25.3mm 的四胞内匹配器件X波段输出功率达到141.25W,线性增益大于12dB,PAE达到41.4%;[5]南京电子器件研究所的任春江,陈堂胜等人,报道了一种采用磁控溅射A1N介质作为绝缘层的的SiC衬底A1GaN/GaN MIS HEMT,器件研制中采用了凹槽栅和场板结构,采用MIS结构后,器件击穿电压由80 V提高到了180V以上,保证了器件能够实现更高的工作电压,在2GHz、75V工作电压下,研制的200μm宽HEMT输出功率密度达到了14.4W/mm,器件功率增益和功率附加效率分别为20.5ldB和54.2%[6]。

2005[1].747.EC 中英文

2005[1].747.EC 中英文

COMMISSION DECISIONof 21 October 2005amending for the purposes of adapting to technical progress the Annex to Directive 2002/95/EC of the European Parliament and of the Council on the restriction of the use of certain hazardous substances in electrical and electronic equipment(notified under document number C(2005) 4054)(Text with EEA relevance)(2005/747/EC)欧盟委员会于2005年10月21日为了适应技术发展,针对指令2002/95/EC附录关于欧盟议会和欧盟理事会在电气电子设备中限制使用某些有害物质进行修改的决定。

THE COMMISSION OF THE EUROPEAN COMMUNITIES, Having regard to the Treaty establishing the European Community, Having regard to Directive 2002/95/EC of the European Parliament and of the Council of 27 January 2003 on the restriction of the use of certain hazardous substances in electrical and electronic equipment (1), and in particular Article 5(1)(b) thereof, Whereas:欧洲共同体委员会,注意到成立欧洲共同体的条约,注意到欧洲议会和欧盟理事会2003年1月27日第2002/95/EC 号关于在电气电子设备(1)中限制使用某些有害物质指令,特别是其中第5(1)(b)条,鉴于:(1) In accordance with Directive 2002/95/EC the Commission is required to evaluate certain hazardous substances prohibited pursuant to Article 4(1) of that Directive.(1)遵照第2002/95/EC号指令,欧盟委员会需要对指令第4(1)条所禁令的某些有害物质进行评估。

俄歇复合、电子泄漏和空穴注入对深紫外发光二极管效率衰退的影响

俄歇复合、电子泄漏和空穴注入对深紫外发光二极管效率衰退的影响
further increases the electron leakage level
[9]
. The
process of Auger recombination is that an electron
recombines with a hole and transfers the recombina-
2. State Key Laboratory of Reliability and Intelligence of Electrical Equipment, Hebei University of Technology, Tianjin 300401, China)
∗Corresponding Authors, E-mail: chuchunshuang@ hotmail. com; zhangyh@ hebut. edu. cn
tion energy to a third carrier in the quantum wells,
which involves three-carrier participation. Therefore, Auger recombination will cause a very remark-
Hole Injection on Efficiency Droop for DUV LEDs
WANG Wei-dong1,2 , CHU Chun-shuang1,2∗ , ZHANG Dan-yang1,2 ,
BI Wen-gang1,2 , ZHANG Yong-hui1,2∗ , ZHANG Zi-hui1,2
(1. 河北工业大学电子信息工程学院 天津市电子材料与器件重点实验室, 天津 300401;
2. 河北工业大学 省部共建电工装备可靠性与智能化国家重点实验室, 天津 300401)

HVPE法制备碳掺杂半绝缘氮化镓晶圆片

HVPE法制备碳掺杂半绝缘氮化镓晶圆片

2021年第9期广东化工第48卷总第443期·13·HVPE法制备碳掺杂半绝缘氮化镓晶圆片赖云1,罗晓菊2,王现英1,2*(1.上海理工大学材料科学与工程学院,上海200093;2.镓特半导体科技(上海)有限公司,上海201306)C-doped Semi-insulating GaN Grown by HVPELai Yun1,Luo Xiaoju2,Wang Xianying1,2*(1.University of Shanghai for Science and Technology,School of Material Science&Engineering,Shanghai200093;2.Eta Research Ltd.,Shanghai201306,China)Abstract:Four-inch self-separated semi-insulating gallium nitride(GaN)wafers were successfully obtained by Hydride Vaper Phase Epitaxy(HVPE)growth with methane as the doping source.The doping gas used is methane gas with a concentration of5%,mixed with N2carrier gas.The thickness of the wafer can reach more than800µm,and the surface roughness is lower than0.6nm without cracks.(002)and(102)of the X-ray diffraction rocking curve half peak width of less than 100arcsec typically were40to60arcsec,curvature radius is more than20m,the dislocation density is lower than106/cm2,the resistivity was measured to be greater than109Ω-cm.Keywords:Hydride vapor phase epitaxy;Gallium nitrides;Crystal growth;Carbon doping;Wafer自支撑氮化镓晶圆片由于其位错密度低、导热系数高、晶格和热膨胀与同质外延结构相匹配,对改善氮化镓基器件(包括LED、激光二极管、电力电子和射频器件)的性能具有重要的影响[1-4]。

2~6_GHz_紧凑型、高效率GaN_MMIC_功率放大器

2~6_GHz_紧凑型、高效率GaN_MMIC_功率放大器

第 21 卷 第 8 期2023 年 8 月太赫兹科学与电子信息学报Journal of Terahertz Science and Electronic Information TechnologyVol.21,No.8Aug.,20232~6 GHz紧凑型、高效率GaN MMIC功率放大器邬佳晟,蔡道民(中国电子科技集团公司第十三研究所,河北石家庄050051)摘要:基于0.25 μm SiC衬底的GaN高电子迁移率晶体管(HEMT)工艺,根据有源器件的Gm a x 和输出功率密度,选择末级功率器件尺寸并确定其最优阻抗;采用三级放大器,其栅宽比为1:4:16,实现高功率增益和高效率;利用等Q匹配技术,把偏置电路融入匹配电路中,实现简单、低损耗和宽带阻抗变换;借助电磁场寄生参数提取技术实现紧凑型芯片版图,尺寸为2.8 mm×2.0 mm。

测试结果表明,偏置条件漏极电压UD =28 V、UG=-2.2 V,在2~6 GHz频率范围内,功率放大器增益大于24 dB,饱和输出功率大于43 dBm,功率附加效率大于45%,可广泛应用于电子对抗和电子围栏等领域。

关键词:紧凑;功率附加效率;宽带;增益;微波单片集成电路中图分类号:TN43;TN722.75 文献标志码:A doi:10.11805/TKYDA20230142~6 GHz compact GaN power amplifier MMICs with high PAEWU Jiasheng,CAI Daomin(The 13th Research Institute,CETC,Shijiazhuang Hebei 050051,China)AbstractAbstract::Based on the 0.25 μm SiC substrate GaN High Electron Mobility Transistor(HEMT)process, the final power device size is selected and its optimal impedance is determined by the Gmaxand the unit output power density of the active device. The tertiary amplifier is adopted, and its gate widthratio is 1:4:16 to achieve high power gain and high efficiency. By using the equal-Q-matching technique,and integraing the bias circuit into the matching circuit, an impedance transformation is realized withsimple, low loss and broadband. With the help of the extraction of parasitic parameters inelectromagnetic fields, the compact chip is realized. The chip size of the Monolithic MicrowaveIntegrated Circuit(MMIC) amplifier is 2.8 mm×2.0 mm. The test results show that in the 2~6 GHzfrequency range, and under the conditions of the drain voltage of 28 V, the gate voltage -2.2 V,andcontinuous wave, the large signal gain of the MMIC amplifier is greater than 24 dB, the saturation outputpower is greater than 43 dBm, and the Power Additional Efficiency(PAE) is greater than 45%. Theproposed paver amplifier can be widely used in electronic countermeasures and electronic fence.KeywordsKeywords::compact;Power Additional Efficiency(PAE);broadband;gain;Monolithic Microwave Integrated Circuit(MMIC)第三代半导体器件GaN因其固有的诸多优势,包括高功率密度、高饱和电子速率、易宽带匹配和好的环境适应能力等,是当前固态微波器件研究的热点[1-4],而宽带、高功率、高效率和高增益的微波单片集成电路(MMIC)功率放大器则一直是电子对抗、电子围栏和雷达通信等领域的关键核心器件,美国等占据领先地位[5-7],WOLFSPEED、QORVO等公司有相关产品报道[8-9],国内则报道较少。

GT2005_68630

GT2005_68630

Proceedings of GT2005ASME Turbo Expo 2005: Power for Land, Sea and AirJune 6-9, 2005, Reno-Tahoe, Nevada, USAPaper Number GT2005-68630 EVALUATION AND CHARACTERIZATION OF IRON- AND NICKEL-BASED ALLOYS FORMICROTURBINE RECUPERATORSEdgar Lara-Curzio, R. Trejo, K. L. More, P. J. Maziasz and B. A. PintMetals & Ceramics DivisionOak Ridge National LaboratoryOak Ridge, TN 37831-6069ABSTRACTThe effects of stress, temperature and time of exposure to microturbine exhaust gases on the mechanical properties and corrosion resistance of alloys HR-120® and 230® was investigated at turbine exhaust temperatures between 620°C and 760°C. It was found that the ultimate tensile strength and ductility of alloy 230® decreased by 30% and 60%, respectively, after 500 hours exposure at 752°C. At the lowest exposure temperature of 679°C the ultimate tensile strength and ductility decreased by 10% and 25%, respectively. The ultimate tensile strength and ductility of HR-120® alloy decreased by 15% and 50%, respectively, after 500 hours exposure at 745°C. At the lowest exposure temperature of 632°C the ultimate tensile strength and ductility decreased by 10% and 23%, respectively. The microstructural changes associated with exposure to microturbine exhaust gases are analyzed and discussed.INTRODUCTIONThe challenging performance targets for the next generation of microturbines include fuel-to-electricity efficiency of 40%, capital costs less than $500/kW, NOx emissions reduced to single parts per million, several years of operation between overhauls, life of 40,000 hours and fuel flexibility [1]. Significant increases in microturbine efficiency can be achieved by increasing engine-operating temperatures, and that can be realized through the use of advanced metallic alloys and ceramics for high-temperature components.One of the critical components of low-compression ratio microturbines is the recuperator, which is responsible for a significant fraction of the overall efficiency of the microturbine [2]. Conventional recuperators are thin-sheet metallic heat exchangers that recover some of the waste heat from the exhaust stream and transfer it to the incoming air stream. The preheated incoming air is then used for combustion because less fuel is required to raise its temperature to the required level at the turbine inlet. Most of today's compact recuperators are manufactured using 300 series (e.g.- 347) stainless steels which are used at exhaust-gas temperatures below about 650° C [3]. At higher temperatures, these materials are susceptible to creep deformation and oxidation, which lead to structural deterioration and leaks, reducing the effectiveness and life of the recuperator. The temperature requirements for the next generation of microturbines have prompted efforts to screen and evaluate candidate materials with the required creep and corrosion resistance. Furthermore, developmental efforts will be needed to adapt current recuperator manufacturing processes to advanced alloys, to reduce costs, and enable long-term reliable operation at higher temperatures.As part of a program sponsored by the U.S. Department of Energy to support microturbine manufacturers in the development of the next generation of microturbines, a recuperator test facility was established at Oak Ridge National Laboratory (ORNL) [4]. The objective of this test facility is to screen and evaluate candidate materials for microturbine recuperators inside a microturbine at turbine exit temperatures (TET) as high as 850°C. Furthermore, the preparation ofsamples for these experiments, which requires welding test specimens to a sample holder, provides the means for identifying potential manufacturability barriers with a particular material.In this paper the results from the evaluation of foils of alloy HR-120® and 230® alloy are presented after exposure in ORNL’s microturbine recuperator testing facility for 500 hours at turbine exit temperatures as high as 785°C. The effect of exposure on the corrosion resistance and tensile strength and ductility and of the material is discussed and the results are compared to those for 347 stainless steel.EXPERIMENTALIn 2001, ORNL acquired a 60kW Capstone microturbine. In collaboration with Capstone Turbine Corp., the microturbine was modified to achieve higher TET values and to allow for the placement of test specimens, through six port bosses, at the entrance of the recuperator. Figure 1 shows a photograph of ORNL’s microturbine recuperator testing facility and a schematic of the modified microturbine indicating the location of the port bosses with respect to the location of the radial recuperator. Further details of ORNL’s microturbine recuperator testing facility can be found elsewhere [4-5].The sample holder onto which the foils under evaluation are laser-welded was 23.1 mm in diameter. Prior to welding the foils, type-K thermocouples were placed in each one of the four holes in the sample holder. Figure 2 shows photographs of sample holders with and without welded foil samples.During exposure tests, the sample holders were subjected to a constant pressure of 60 psi (0.41 MPa) to reproduce the state of stress that recuperator cells experience during normal microturbine operation. This pressure corresponds to the difference between the pressure of compressed air on one side of the cell and the pressure of the exhaust gases on the other. The pressure inside the sample holder is controlled using a computerized system for the duration of the test. This system also provides the means for determining whether an increase in volume in the sample holder has occurred, which would be associated with creep deformation or rupture of the foils has occurred.During exposure tests, the sample holders are subjected to a temperature gradient as illustrated by the temperature profile depicted in Figure 3, which is for a nominal TET value of 800°C. For this case the temperature along the length of the sample holder varies between 650°C and 760°C. The temperature gradient, which results from the configuration of the microturbine, allows for the evaluation of materials over a wide range of temperatures during the same test. Table I summarizes the microturbine settings used for the test.The material investigated in this study included alloys HR-120® and 230® alloy. These are chromia-forming austenitic nickel-based alloys developed by Haynes International Inc. Tables II and III list the composition of these alloys and the thickness of the foils that were evaluated in this study.Figures 4 and 5 show backscattered scanning electron (BSE) images of cross-sections of foils of alloys HR120® and 230®. The presence of tungsten carbide particles in alloy 230® is evident in the micrographs in Figure 4. It can also be observed that the smaller tungsten carbide particles tend to be aligned along planes parallel to the rolling direction.The baseline mechanical properties of the materials investigated in this study were determined at ambient temperature. Miniature dog-bone shaped tensile specimens were obtained by electron discharge machining from foils 20.3 cm wide. Test specimens were obtained with their main axis either parallel or perpendicular to the rolling direction. The dimensions of the dog-bone shaped miniature tensile specimens were 10 mm long, with a gauge section 1.27-mm wide and 3.8-mm long. Figure 6 shows a typical test specimen. The tensile stress-strain behavior of the miniature test specimens was determined under a constant crosshead displacement rate of 0.01 mm/min using an electromechanical testing machine. A special set of grips and alignment fixture were used to transfer the load to the test specimens and to ensure alignment to eliminate spurious bending strains. Because of the small dimensions of the test specimens it was not possible to determine the strain directly. However, the tensile strain of the test specimens was estimated after correcting the recorded crosshead displacement from the contribution of the machine compliance to the recorded displacement. Values for the 0.2% yield stress, ultimate tensile strength and strain failure were obtained from each stress-strain curve. These results are listed in Table IV. Data reported by the material manufacturer are listed in Table V.At the end of 500-hr exposure tests the sample holders were removed from the microturbine, and the foils were cut from the sample holder. Miniature tensile test specimens were obtained from the foils by electron discharge machining. Other pieces of the foil were used for microstructural characterization and compositional analysis using an electron-probe microanalyzer (EPMA). While special precautions were taken to preserve the integrity of the oxide scale that formed on the surface of the foils evaluated, it was not possible to know if any material had spalled off prior to the removal of the sample holders from the microturbine.RESULTS AND DISCUSSIONAlloy 230®Figure 7 presents a picture of the sample holder with alloy 230® foils at the end of the 500-hr exposure test. Under regular lighting conditions the foils had a dull appearance and grew darker with exposure temperature. There was no evidence of creep deformation, in contrast to the ballooning experienced by foils of 347 stainless steel exposed to similar conditions [5].Figure 8 presents scanning electron micrographs of the cross-sections of foils that had been exposed for 500 hours. For the case of the foil exposed at 752°C, which was located in position 1 of the sample holder, it was found that only a very thin layer of chromium oxide was present on the surface (Figure 8d). It was also found that a series of intergranular cracks, which were several micrometers long and had spanned more than one grain, had developed on the side of the foil that had been exposed to the microturbine exhaust gases. Smaller cracks were also observed on the surface of the foils that had been exposed to compressed air. Similar to the foil that hadbeen exposed to the highest temperature (752°C), short cracks had formed along the grain boundaries on the surface of foils that had been exposed to the microturbine exhaust gases at lower temperatures (736°C, 700°C and 679°C). Figures 8a to 8c depict scanning electron micrographs of the cross-section of these foils. Smaller cracks were also found to form on the surface that had been exposed to compressed plant air. Elemental maps (Figure 9), obtained from foils exposed to 752°C and depicted in Figure 8, showed that the surfaces of those cracks were rich in oxygen and deficient in chromium. The depletion of chromium from the grain boundaries of the base metal near the surface is evident in the elemental maps obtained. It is believed that the sub-surface degradation and cracking of the material resulted from Cr depletion and precipitation of Cr-rich carbides. Similar observations have been reported by Gleeson and Harper reported for 230® alloy after cyclic oxidation for 720 days at 982°C [6].Figure 10 presents the stress versus strain curves from the tensile evaluation of miniature test specimens obtained from the foil at location 1 (752°C) of the sample holder. Also included are stress-strain curves for the as-received material. It was found that the ultimate tensile strength and ductility of 230® alloy decreased by 30% and 60%, respectively, after 500 hours exposure at 752°C. At the lowest exposure temperature of 679°C the ultimate tensile strength and ductility decreased by 10% and 25%, respectively. Table VI summarizes the tensile results.The loss of ductility of 230® alloy after exposure to microturbine exhaust gases is most likely the result of carbide precipitation. Storey et al. reported that the precipitation of large M6C carbides and smaller grain boundary M23C6 precipitates were responsible for the 30% decrease in ductility experienced by alloy 230® after 1500-hour long exposures at 760°C [7]. These authors also reported that a heat treatment at 1177°C for 3 hours was sufficient to re-dissolve the embrittling phases without grain growth and to restore as-processed ductility values.The relationship in Equation 1 was found to provide a good representation of the ultimate tensile strength of alloy 230® foils as a function of 500-hr exposure temperature in ORNL’s microturbine.s s o =1-T900ÊËÁˆ¯˜7.5(1)where s is the ultimate tensile strength at the exposure temperature T (in degrees Celsius) and s o is the tensile strength at 20°C.Alloy HR-120®Figure 11 shows the sample holder with HR-120® alloy foils at the end of the 500-hr exposure in ORNL’s microturbine. Under regular lighting conditions the appearance of the foils in locations 2, 3 and 4 of the sample holder was “shiny” and brass-looking. The foil that had been exposed to the highest temperature had a dark, dull appearance.Figure 12 presents BSE images of cross-sections obtained from HR-120® alloy foils after 500-hr microturbine exposure. A thin multiphase oxide scale had formed and it was thicker on the surface exposed to the exhaust gases. An elemental compositional map (Figure 13) revealed that the grain boundaries closest to the surface and just below the surface exposed to the exhaust gases had been depleted of chromium and enriched in nickel. In the case of HR-120® alloy foils, the oxide scale possesses a multilayered structure consisting of mixed oxides of silicon, chromium and iron.Gleeson and Harper reported that a Si-rich oxide scale formed on HR-120® alloy after cycling oxidation for 720 days in air at 982°C [6]. They also reported the depletion of chromium in the base metal near the surface and the formation of scales containing Cr2O3+NiCr2O4and NiO after thermal cycling at temperatures above 1093°C. At temperatures above 1200°C, they reported the presence of a fast-growing Fe3O4 oxide.Figure 14 presents the stress versus strain curves obtained from the tensile evaluation of the miniature test specimens of HR-120® alloy before and after 500-hr long exposure in ORNL’s microturbine recuperator testing facility. It was found that the ultimate tensile strength and ductility of the HR-120® alloy decreased by 15% and 50%, respectively, after exposure at 745°C. At the lowest exposure temperature of 632°C the ultimate tensile strength and ductility decreased by 10% and 23%, respectively. Table VII summarizes the tensile results.The temperature dependence of the ultimate tensile strength for the HR-120® alloy after 500-hr exposure in ORNL’s microturbine was found to be well described by Equation 2:ss o=1-T1000ÊËÁˆ¯˜6(2)Preliminary analyses of the behavior of alloy HR-120® suggest that the decrease in ductility after exposure in microturbine results from the precipitation of Cr-rich (M23C6) carbides [8].Figure 15 compares the effect of temperature of exposure in ORNL’s microturbine recuperator testing on the tensile strength of 347 stainless steel and alloys 230® and HR-120®. It was found that among the three alloys, HR-120® exhibits the best retention of tensile strength, followed by alloy 230® and 347 stainless steel. Equation (3) was found to describe well the temperature dependence of the ultimate tensile strength of 347 stainless steel after a 500-hr long exposure [5].ss o=1-T825ÊËÁˆ¯˜9.4(3)While there are no fundamental basis behind the form of the correlations in Equations 1-3, it is interesting to observe that a larger denominator and a smaller exponent are associated with increasing resistance to exposure to microturbine exhaust gases. These correlations are plotted, along with the experimental results in Figure 15. A detailed analysis of the effect of exposure to microturbine exhaust gases on theproperties and microstructure of 347 stainless steel can befound elsewhere [5].SUMMARYA test facility for screening and evaluating candidate materials for the next generation of microturbine recuperators has been designed and is operational at Oak Ridge National Laboratory. The core of the test facility is a 60kW Capstone microturbine, which was modified to operate at higher turbine exit temperatures and to allow the placement of test specimens at the entrance of its radial recuperator. Sample holders have been designed and instrumented to allow for the continuous recording of the temperature of the thin metallic foil test specimens and to subject these to mechanical stresses through the internal pressurization of the sample holder. Materials under evaluation are welded to the sample holder using laser or e-beam techniques and allow for the identification of potential problems in manufacturability.Results have been presented from the evaluation of 89-µm and 102-µm thick foils of alloys 230® and HR-120®. It was found that the ultimate tensile strength and ductility of alloy 230® decreased by 30% and 60%, respectively, after 500 hours exposure at 752°C. At the lowest exposure temperature of 679°C the ultimate tensile strength and ductility decreased by 10% and 25%, respectively. Alloy 230® experienced cracking on the surface exposed to the microturbine exhaust gases and the length of those cracks grew with exposure temperature. The grain boundaries in the base metal near the surface were found to be depleted of chromium.The ultimate tensile strength and ductility of HR-120® alloy decreased by 15% and 50%, respectively, after 500 hours exposure at 745°C. At the lowest exposure temperature of 632°C the ultimate tensile strength and ductility decreased by 10% and 23%, respectively. A layered scale comprised of oxides of nickel, chromium, iron and silicon were found to have formed on the surface of HR-120® alloy foils that were exposed to the microturbine exhaust gases. While silicon was found to be present both inside grains and at grain boundaries, it was found that grain boundaries near the interface between the base metal and the oxide scale had been depleted of chromium. Alloy HR-120® was found to exhibit the greatest resistance to exposure to microturbine exhaust gases, followed by alloy 230® and 347 stainless steel. ACKNOWLEDGMENTSResearch sponsored by the U.S. Department of Energy, Assistant Secretary for Energy Efficiency and Renewable Energy, Distributed Energy Program, as part of the Advanced Microturbine Program, under contract DE-AC05-00OR22725 with UT-Battelle, LLC. The contributions from Mr. Randy Parten are greatly appreciated.REFERENCES1.“Advanced Microturbine Systems Program, Plan ForFiscal Years 2000 Through 2006,” U.S. Department of Energy, Office of Energy Efficiency and Renewable Energy, Office of Power Technologies. March 2000.2. C. F. McDonald, “Heat Recovery Exchanger Technologyfor Very Small Gas Turbines,” Intl. Journal of Turbo and Jet Engines,” vol. 13 (1966) pp. 239-261.3.O. O. Omatete, P. J. Maziasz, B. A. Pint, and D. P. Stinton,“Assessment of Recuperator Materials for Microturbines,”ORNL/TM-2000-304.ra-Curzio, E., Maziasz, P. J., Pint, B. A., Stewart, M.,Hamrin, D., Lipovich, N. and DeMore, D., 2002, “Test Facility for Screening and Evaluating Candidate Materials for Advanced Microturbine Recuperators,” ASME Paper #2002-GT-30581, presented at the International Gas Turbine & Aeroengine Congress & Exhibition, Amsterdam, Netherlands, June 3-6, 2002.5. E. Lara-Curzio, R. M. Trejo, K. L. More, P. J. Maziasz,and B. A. Pint, “Screening and Evaluation of Materials for Advanced Microturbine Recuperators,” Proceedings of ASME Turbo Expo 2004, June 14-17, 2004 Vienna, Austria, Paper GT-2004-54255.6. B. Gleeson and M. A. Harper, “The Long-Term, Cyclic-Oxidation Behavior of Selected Chromia-Forming Alloys,”Oxidation of Metals, vol. 49, Nos. 314 (1998) pp. 373-399 7.I. J. Storey, D. L. Klarstrom, G. L. Hoback, V. R. Ishwarand J. I. Qureshi, “The Metallurgical Background to Rejuvenation Heat Treatments and Weld Reparability Procedures for Gas Turbine Sheet Metal Components,”Materials at High Temperatures18 (4) pp. 241-247 (2001)8.P. J. Maziasz, John P. Shingledecker, Bruce A. Pint, NealD. Evans, Y. Yamamoto, K. L. More andE. Lara-Curzio,“Overview Of Creep Strength And Oxidation Of Heat-Resistant Alloy Sheets And Foils For Compact Heat-Exchangers,” Proceedings of ASME Turbo Expo 2005, June 6-9, 2005, Reno, Nevada, Paper GT2005-68927Table I. Microturbine settings for 500-hr test.Engine Speed 45,000 RPMTurbine Exit Temperature 800°CSample holder pressure 60 psiFuel naturalgasTable II. Composition of 230® alloy (wt. %)(Haynes International, Kokomo, IN 46904)Element Concentration Element Concentration Element Concentration Ni 57(balance) Mo 2 Al 0.3 Cr 22 Mn 0.5 C 0.1 W 14 Si 0.4 La 0.02 Co 5 (max) Fe 3 (max) B 0.015 (max)Table III. Composition of HR-120® alloy (wt. %)(Haynes International, Kokomo, IN 46904)Element Concentration Element Concentration Element Concentration Ni 37 Mo2.5(max)Al 0.1 Cr 25 Mn 0.7 C 0.05 W2.5(max)Si 0.6 Cb 0.7 Co 3 (max) Fe 33 (balance) B 0.004N 0.2Table IV. Summary of tensile results for as-received materials. Values correspond tomean values ± one standard deviation.230® alloy 0.2% YieldStrength (MPa) Ultimate TensileStrength (MPa)FailureStrain (%)0.089-mm thick⊥ to rolling direction 452± 24 780 ± 18 36 ± 4 || to rolling direction 422 ± 12 770 ± 11 34 ± 20.102-mm thick⊥ to rolling direction 466 ± 23 817 ± 12 40 ± 4 || to rolling direction 489 ± 45 818 ± 27 36 ± 3HR-120® alloy0.089-mm thick|| to rolling direction 373 ± 31 697 ± 4 37 ± 5Table V. Tensile Properties of 230® alloy (hot-rolled and 1232°C solution annealed plate) and alloy HR-120® (solution heat-treated plate)(Haynes International, Kokomo, IN 46904)Yield strength at 0.2% Offset (MPa) Tensile strength(MPa)Elongation(%)230® alloy 375 840 48HR-120® alloy 375 735 50Table VI. Summary of tensile results for 230® alloy. Values correspond to mean values± one standard deviation.Foil Thickness(mm) T (°C) 0.2% σy(MPa)UTS (MPa) Failurestrain (%)1 0.089 752 415 ± 12 561 ± 28 13.0 ± 3.02 0.102 736 457 ± 15 660 ± 34 19.0 ± 3.43 0.089 700 418 ± 41 644 ± 24 19.0 ± 2.94 0.102 679 481 ± 7.1 728 ± 22 27.0 ± 6.3Table VII. Summary of tensile results for HR-120® alloy. Values correspond to meanvalues ± one standard deviation.Foil T(°C) 0.2%σy(MPa) UTS (MPa) Failurestrain (%)1 745 388 ± 35 594 ± 32 18.0 ± 4.42 730 421 ± 37 615 ± 30 21.0 ± 4.43 700 408 ± 39 582 ± 48 23.0 ± 4.74 632 407 ± 27 631 ± 53 29.0 ± 4.7(a)(b)Figure 2. Sample holders for exposure of metallic foils in ORNL’s microturbine recuperator testing facility. The orifices where thermocouples are placed and that are used to allow mechanical stressing of test specimens through pressurization is shown on the left. A sample holder with laser-welded metallic foils is shown on the right.Figure 3. Temperature distribution along sample holder for a TET =800°C.(a) (b)Figure 4. BSE image of (a) 89-µm and (b) 102-µm thick foils of 230® alloy. Grain structure and large W-rich particles (bright particles) are clearly visible. Voids inside W-rich particles likely form during polishing.Figure 5. BSE image of 89-µm thick foil of HR-120®. The grain structure and large Nb-rich particles (bright white) are clearly visibleFigure 6. Miniature tensile test specimen for evaluation of mechanical properties of metallic foils. Tests specimens are obtained by electron-discharge machining.Figure 7. Sample holder with 230® alloy foils after 500-hr exposure in ORNL’s microturbine recuperator testing facility at TET=800°C.exhaust gas surface(a) 679°C (b) 700°Cexhaust gas surface(c) 736°C (d) 752°CFigure 8. BSE images of 230® alloy: (a) 89-µm thick foil; (b) 102-µm thick foil; (c) 89-µm thick foil; (d) 102-µm thick foil.Figure 9. BSE image and corresponding elemental maps obtained from a 89-µm thick foil of 230® alloy after a 500-hr long exposure at 752°C in ORNL’s microturbine recuperator testing facility. Surface at the top of the micrographs had been exposed to the microturbine exhaust gases. Note the depletion of chromium along the grain boundaries near the surface. Grain boundaries in the bulk are rich in chromium and Ni-depleted.microturbine recuperator testing facility at TET=800°C.exhaust gas surface(a) 632°C (b) 700°Cexhaust gas surface(c) 730°C (d) 745°CFigure 12. BSE images of cross-sections obtained from 89-µm thick HR-120® alloy foils after 500-hr exposure at TET=800°C. The upper surface in the micrograph had beenexposed to the microturbine exhaust gases.Figure 13. BSE image and corresponding elemental maps from cross-sectional area of 89-µm thick HR-120® alloy foil that was exposed for 500 hours at 745°C. The upper surface in the micrograph had been exposed to the microturbine exhaust gases. Note that the grain boundaries near the surface are poor in chromium but rich in nickel.Figure 14. Tensile stress-strain results obtained from the evaluation of miniature tensileFigure 15. Effect of temperature on the ultimate tensile strength of 347 stainless steel and alloys 230® and HR-120® after 500-hr exposure in ORNL’s microturbine recuperatortesting facility.。

High-efficiency-CH3NH3PbI-3-x-Clx-perovskite-solar-cells-with-poly-

High-efficiency-CH3NH3PbI-3-x-Clx-perovskite-solar-cells-with-poly-

Short communicationHigh efficiency CH3NH3PbI(3Àx)Cl x perovskite solar cellswith poly(3-hexylthiophene)hole transport layerFrancesco Di Giacomo a,1,Stefano Razza a,1,Fabio Matteocci a,Alessandra D’Epifanio b, Silvia Licoccia b,Thomas M.Brown a,Aldo Di Carlo a,*a CHOSE e Center for Hybrid and Organic Solar Energy,Department of Electrical Engineering,University of Rome“Tor Vergata”,via del Politecnico1, 00133Rome,Italyb Department of Chemical Science and Technologies,University of Rome“Tor Vergata”,Via della Ricerca Scientifica00133Rome,Italyh i g h l i g h t sPerovskite solar cells with doped P3HT hole transporter were fabricated.For thefirst time doped P3HT was used with CH3NH3PbI(3Àx)Cl x perovskite.Best cells showed efficiency up to9.3%,the record for P3HT solar cells.Doped P3HT cells showed a high V OC up to1.01V.TiO2dehydration step has been introduced in device fabrication process.a r t i c l e i n f oArticle history:Received10September2013 Received in revised form8November2013Accepted15November2013 Available online1December2013Keywords:Perovskite solar cellDoped P3HTThinfilm photovoltaics Organometal Halide Perovskite a b s t r a c tWe fabricate perovskite based solar cells using CH3NH3PbI3Àx Cl x with different hole-transporting ma-terials.The most used2,20,7,70-tetrakis-(N,N-di-p-methoxyphenylamine)9,90-spirobifluorene(Spiro-OMeTAD)has been compared to the poly(3-hexylthiophene-2,5-diyl)(P3HT).By tuning the energy level of P3HT and optimizing the device’s fabrication,we reached9.3%of power conversion efficiency,which is the highest reported efficiency for a solar cell using P3HT.This result shows that P3HT can be a suitable low cost hole transport material for efficient perovskite based solar cells.Ó2013Elsevier B.V.All rights reserved.1.IntroductionNowadays,photovoltaic(PV)materials and associated manufacturing processes are under intensive research and devel-opment[1]to increase device efficiency,reduce cost and enable new applications for solar energy.In fact,even though silicon solar cells have reached efficiencies of up to25%for single crystal Si[2] and20.4%for multi-crystalline Si[3],the production of such ma-terial requires energetically demanding processes(such as Si ingot purification)and relatively expensive production lines[4].On the other hand,thinfilm technologies have been proved[5]to reduce material costs and energy payback time.Amorphous silicon,CdTe and Cu(In,Ga)Se2technologies have been extensively investigated [5]and have already found commercial application.More recently, new concepts for delivering solution-processed photovoltaics have been introduced to further simplify the manufacturing process to increase fabrication throughput and reliability and to reduce cost. Among solution based photovoltaics,Dye Solar Cells(DSC)repre-sent a new class of electrochemical solar cells[6]based on sensi-tized mesoporous TiO2,a liquid electrolyte and a catalyst layer in a sandwich-like architecture.This kind of device allows achievement of efficiencies of up to12.3%[7]whilst using simple production processes and equipment.However,the liquid electrolyte may still be problematic[8,9]for the production and stability of devices.In this class of cells,solid state DSCs(SDSCs)have been proposed to replace the liquid electrolyte with a hole transport material(HTM). The most commonly used HTM is(2,20,7,70-tetrakis-(N,N-di-p-*Corresponding author.Tel.:þ39(0)672597456.E-mail address:aldo.dicarlo@uniroma2.it(A.Di Carlo). 1Both authors contributed equally to thiswork.Contents lists available at ScienceDirect Journal of Power Sourcesjournal ho mep age:www.elsevi /locate/jpowsour0378-7753/$e see front matterÓ2013Elsevier B.V.All rights reserved./10.1016/j.jpowsour.2013.11.053Journal of Power Sources251(2014)152e156methoxyphenylamine)9,90-spirobifluorene)(Spiro-OMeTAD)[10], which presents efficient charge transport,low recombination rates and also good porefilling of the TiO2layer enhancing device per-formance with respect to polymer HTMs.For the sake of lowering costs of the technology,poly(3-hexylthiophene-2,5-diyl)(P3HT) has been employed as a cheaper alternative for small[11]and large area[12]devices.This material shows relatively high hole mobility and can be deposited with several kinds of coating techniques [13,14],such as spin coating,spray coating,slot dye,inkjet printing, and electro-polymerization.Two main issues are commonly linked to P3HT.The size of the polymeric chain reduces the porefilling of the mesoporous TiO2layer[15],limiting the maximum thickness of TiO2layer and thus of dye absorption.Furthermore,a tight control of coating parameters and on the additives used is needed to ach-ieve the regular morphology required to improve interchain hop-ping.By controlling these factors P3HT devices with Power Conversion Efficiency(PCE)of up to4.5%have been fabricated[16].Recently,a new class of hybrid organic halide perovskite was introduced as light harvesting material,showing strong absorption in a broad region of the visible spectrum(direct energy gap down to w1.55eV[17]),good electron and hole conductivity,delivering also high open circuit voltages in photovoltaic devices.A PCE of10.2% has been reported[18]using a CH3NH3PbI3Àx Cl x sensitized TiO2 together with Spiro-OMeTAD as HTM.By replacing TiO2with Al2O3 a PCE of12.3%was obtained[19].In the latter case,the electrons are transported directly by the perovskite layer,which is anchored to a mesoporous Al2O3scaffold.Remarkably,this kind of perovskite can be processed in air,which makes it a good candidate for industrial use.Another way to improve the performance of TiO2/perovskite solar cells is to modify the TiO2surface using a self-assembled monolayer of C60fullerenes[18]reaching11.7%PCE with Spiro-OMeTAD and6.7%PCE with P3HT,while without C60the effi-ciency was10.2%and3.8%,respectively.Regarding the HTM ma-terial coupled with a CH3NH3PbI3perovskite,alternatives to Spiro-OMeTAD have been explored[20]reaching12%efficiency with poly-triarylamine(PTAA)and6.7%with P3HT.The high efficiency reached with PTAA already showed how polymer HTMs can lead to similar or even superior performance when systematically compared to Spiro-OMeTAD since porefilling by the HTM is not required anymore in this type of cell where the TiO2is capped by a layer of perovskite.However,the highest efficiency with perovskite materials was still obtained with Spiro-OMeTAD in the last works which showed efficiency equal or higher than15%[21,22].On the other hand,in these works the perovskite synthesis was different to the standard procedures and no comparison with polymeric HTM was performed.In this paper,we show how P3HT can be a suitable HTM for efficient perovskite based solar cells.We propose an FTO/TiO2/ CH3NH3PbI3Àx Cl x/P3HT/Au architecture(scheme reported in Fig.S1)with the intention of optimizing the performance of P3HT based perovskite solar cell.For thefirst time doped P3HT is used in combination with CH3NH3PbI3Àx Cl x,reaching afinal device effi-ciency of9.3%,which is,to the best of our knowledge,the highest reported efficiency for a solar cell using P3HT as a hole extractor and transporter.In order to assess results,we compare the P3HT cells with similar ones made with Spiro-OMeTAD.The use of P3HT, albeit showing a higher recombination rate respect to Spiro-OMeTAD[23],permits an easy,low cost scaling up of the cell promoting industrial exploitation of this technology.2.ExperimentalIn order to create the desired electrode pattern,FTO/glass sub-strates(Pilkington,8U,À1,25mmÂ25mm)were etched via raster scanning laser(Nd:YVO4pulsed at30kHz average output power P¼10W),4cells were formed on each substrate.Patterned substrates were cleaned by ultrasonic bath,using detergent, acetone and isopropanol.A compact TiO2film was deposited onto the FTO surface by Spray Pyrolysis Deposition(SPD)technique us-ing a previously reported procedure[16].Onto the substrates with the TiO2compact a thinfilm of TiO2nanoparticles based paste (18NR-T Dyesol diluted with terpineol,ethilcellulose,isopropanol and ethanol)was screen-printed and successively sintered at 480 C for30min.Thefinal thickness of the n-TiO2film was measured via profilometer(Dektak Veeco150).Profiles were smoothed using Origin8.5Software.To dehydrate the samples, these were heated at120 C for60min in oven.UV irradiation was performed with an estimated power density of225mW cmÀ2 (Dymax EC5000UV lamp with a metal-halide bulb PN38560 Dymax that contains no UV-C).Methylammonium iodide was synthesized following a previ-ously reported procedure[24],while PbCl2(Aldrich,98%)was used as received.The perovskite was deposited by spin coating (2000rpm for60s)from a dimethylformamide(DMF)solution of methylammonium iodide and PbCl2(3:1M ratio)in ambient con-dition which formed the perovskite after heating to120 C for 60min and a second profile was measured.There was no control over the humidity during the fabrication and characterization processes.The mean humidity was equal to60%and ambient temperature was25 C.The hole-transporting material(HTM)was deposited in thefirst case by spin coating a solution of2,20,7,70-tetrakis-(N,N-dip-methoxyphenylamine)9,90-spirobifluorene(Spiro-OMeTAD)at 2000rpm for60s in ambient condition and left in air overnight in a closed box containing silica desiccant.In the second case,the hole-transporting layer was obtained by a spin coating in nitrogen at-mosphere(glove box)a P3HT solution in chlorobenzene(Merck 15mg mLÀ1,MW¼94,100g molÀ1),with the following parame-ters:600rpm for12s andfinally at2000rpm for40s.LiN(CF3-SO2)2N(25mM,Aldrich)and4-tert-butylpyridine(TBP,76mM) were added to both HTM solutions on the spin coating solution. After HTM deposition a third profile was measured.Samples were introduced into a high vacuum chamber(10À6mbar)in order to evaporate Au back contacts(thickness100nm)by thermal evap-oration.An evaporation mask defined a device area of0.1cm2 (2Â5mm).Masked devices(3Â6mm aperture)were tested under a solar simulator(KHS Solar Contest1200Class B)at AM1.5and 100mW cmÀ2illumination conditions calibrated with a Skye SKS 1110sensor,using a Keithley2420as a source-metre in ambient condition without sealing.Sun simulator spectrum was measured with a BLACK-Comet UV e VIS Spectrometer(range190e900nm). The sun simulator is class B in the visible and near-infrared range (class B between700and800nm and class A in the rest of the400e 1100nm range)and has a spatial uniformity less thanÆ5%.Incident photon-to-current conversion efficiency(IPCE)was measured us-ing an apparatus made of an amperometer(Keithley2612)and a monochromator(Newport Mod.74000).UV e vis spectra were measured with a Shimadzu UV-2550(PC)/MPC2200spectropho-tometer together with an integrating sphere.X-ray diffraction (XRD)analysis was performed to investigate the phases of the samples,using a Philips X-Pert Pro500diffractomer with Cu Ka radiation.3.Results and discussionThe compact TiO2(c-TiO2)synthesis process and thickness were previously optimized[16]on an SDSC for efficient charge collection and for avoiding recombination of electrons from the FTO back into the active layer.Adding acetylacetone(ACAC)to a conventionalF.Di Giacomo et al./Journal of Power Sources251(2014)152e156153precursor solution for spray pyrolysis deposition of c-TiO 2layers has been shown to enhance the blocking effect and consequently of the diode-like behaviour of the cell.This is crucial to avoid any current loss at the FTO interface.ACAC enhances the adhesion of c-TiO 2over the FTO reducing the charge transfer resistance at their interface.The compact layer thickness we used is larger than most found in the literature for perovskite solar cell (120nm respect to 50e 60nm [19,20]).P3HT was blended with LiN(CF 3SO 2)2N (Lithium TFSI)salt and tert-butylpiridine.These additives are used in SDSCs to improve device ef ficiency by doping the HTM,and have also been used on perovskite solar cells [20,23].Further optimiza-tions were performed on the TiO 2paste formulation and a pre-treatment was introduced on the sintered porous TiO 2.To obtaina thickness of 700nm by screen printing we diluted the commercial 18NR-T Dyesol paste.If the dilution was performed only with ethanol a very rough surface was obtained,so the 18NR-T paste was blended with a mixture of terpineol,ethylcellulose,isopropanol and ethanol in order to preserve the thixotropic behaviour and to allow the formation of a flat TiO 2layer.Since it is well known that this class of perovskites is very unstable in the presence of moisture [25],due to the presence of the hygroscopic amine salt,a further improvement was obtained by dehydration of the TiO 2prior to spin coating the perovskite solution.Dehydration was performed by heating the sintered TiO 2at 120 C for at least 1h.To maintain dehydration,the samples were kept in a dry environment while cooling to room temperature.To further clean the TiO 2surface [26],some samples were UV irradiated with 200mW cm À2incident power using an Hg lamp.The perovskite absorbance spectra are shown in Fig.1for all the different samples.An increase in the absorbance can be noticed for the dehydrated samples,while the UV-treated samples showed smaller absorbance.The reason for the lower absorbance can be ascribed to the hydrophilic behaviour of the TiO 2induced by the UV treatment [27],which increases the absorption of water on the titania surface.The perovskite layer was further characterized with X-ray diffraction analysis shown in Fig.S2,All characteristic diffraction peaks of the perovskite struc-ture were observed at angles of 14.17 ,28.38 40.5 and 43.1 which suggest that the films fabricated on glass substrates were single phase.By adopting all the previous optimization steps,a batch of 66devices using P3HT and Spiro-OMeTAD was realized and the PCE and open circuit voltage (V OC )are shown in Fig.2,while fill factor (FF)and short circuit current (J SC )are shown in Fig.S3.The PCE and open circuit voltage (V OC )histograms allowed us to statistically characterize the P3HT devices also in comparison with the Spiro based cells.For each histogram a Gaussian fit of the distribution was also plotted.The average ef ficiency of P3HT devices was (6.6Æ1.7)%while the most ef ficient cell had a PCE of 9.3%.These values are very close to the Spiro-OMeTAD based cells,which reach an average PCE of (5.9Æ1.3)%.We obtained several devices with ef ficiency overtheFig.1.Absorbance spectra of TiO 2/CH 3NH 3PbI (3Àx )Cl x on FTO glass.The black line is relative to a dehydrated TiO 2sample,the light grey to a UV-treated sample,and the dark grey to a sample without any treatment.TiO 2thickness was equal to 700nm and a 40%w/w perovskite precursor solution was spin coated at 2000RPM and annealed at 120 C for 1h.All measurements were carried out using an integrating sphere.Absorbance of FTO/glass was subtracted for allsamples.Fig.2.Histograms of the PCE (left side)and V OC (right side)for a single batch of 66solar cells with an FTO/c-TiO 2/nc-TiO 2/CH 3NH 3PbI (3Àx )Cl x /HTM/Au architecture,with P3HT (red bar upper side)and Spiro (black bar lower side)as HTM.(For interpretation of the references to colour in this figure legend,the reader is referred to the web version of this article.)F.Di Giacomo et al./Journal of Power Sources 251(2014)152e 156154previously reported record[20]for P3HT based device.Regarding the other PV parameters,both kind of devices showed similar FF, 60Æ5%for Spiro and58Æ5%for P3HT,and J SC,12Æ2mA cmÀ2for Spiro and12Æ3mA cmÀ2for P3HT,while there is a clear enhancement of V OC in the P3HT devices.In fact,the V OC of P3HT devices is0.93Æ0.06V which is higher than0.84Æ0.03V obtained with Spiro-OMeTAD(an8%average increase).This phenomenon can be ascribed to the different ionization potentials(HOMO)of the HTMs(5.0e5.1eV for Spiro[28]and5.1e5.2eV for P3HT[29]) together with a photoinduced oxidative p-doping of the P3HT [30,31],which can further increase the ionization potential.Even in this latter case,hole injection from the perovskite to the HTM is possible since the valence band of CH3NH3PbI3Àx Cl x lies at 5.3eV[32].In Fig.3the JV curves for the best P3HT and Spiro-OMeTAD based cells(9.3%and8.6%PCE,respectively)are reported.The two curves are very similar in all characteristics besides the V OC.To further characterize the two devices,the series resistance and the shunt resistance were measured by evaluating the slope of the JV curves at open circuit and short circuit conditions,respectively.Theresults showed that while the series resistances of the devices are equal(8U cm2for both),the shunt resistances are slightly different (295U cm2for P3HT and365U cm2for Spiro-OMeTAD),due to the higher recombination rate of P3HT[23]as HTM.However,the significant increase of the V OC discussed earlier results in a more efficient P3HT device.To further characterize the cells’architecture,the thickness of the multilayer was recorded after each deposition step(sintered mesoporous TiO2over the c-TiO2,annealed perovskite,and dried P3HT)starting from the edge of the sample(clean FTO area)to-wards the centre of the cell.Each thickness profile was taken along the same line to study the deposition of each layer on the previous one.Results shown in Fig.4can be gauged considering the device architecture reported in Fig.S1.Thefirst step present between2700 and3500m m is relative to the120nm thick TiO2compact layer.The mesoporous TiO2layer overlaying the compact layer is700nm thick.The thickness profile of the perovskite layer shows a high roughness over the TiO2layer,meaning that the part of the perovskite material raises above the mesoporous structure.Since the thickness profile after the subsequent P3HT deposition shows a muchflatter surface,it is possible that the roughness of the perovskite had arisen from the profilometer’s tip collecting mate-rial during profiling,or from weakly bonded perovskite crystals which were then removed by spin coating the P3HT overlayer.The presence of this perovskite capping layer(already reported in literature[19,20])led to efficient P3HT based devices compared to a solid state DSC,since there is no strict requirement of porefilling into the TiO2structure.Indeed the PCE of the P3HT based devices is very similar if not greater than the equivalent Spiro-OMeTAD based cells.On the other hand,if the same comparison is made with SDSCs,a47%PCE lowering using P3HT instead of Spiro-OMeTAD was reported[33].These results show that P3HT,as well as PTAA, can be a suitable HTM for efficient and low cost perovskite based solar cells,thanks to an appropriate HOMO level and because pore filling is not a requirement for this type of cells.4.ConclusionWe showed how doped P3HT can be a suitable HTM for efficient perovskite based solar cells,fabricating devices with PCE up to9.3% and high V OC.This PCE is,to the best of our knowledge,the highest reported efficiency for a solar cell using P3HT as a hole extractor and transporter.Further efficiency enhancements may be achieved by replacing TiO2with Al2O3,which has been shown[24]to improve the overall performance of cells.Other improvements can be sought by tailoring the perovskite composition(e.g.Br addition [25])or by using the recently developed two-step synthesis[21]. AcknowledgementsThanks are due to Ms C.D’Ottavi for her valuable technical support.The authors thank Dr Girolamo Micuzzi for laser etching, Martina Dianetti for Au evaporation and Andrea Zampetti for useful discussion.We acknowledge“Polo Solare Organico”Regione Lazio and the“DSSCX”MIUR-PRIN2010for funds.F.Di Giacomo and S. Razza contributed equally to this work.Appendix A.Supplementary dataSupplementary data related to this article can be found at http:// /10.1016/j.jpowsour.2013.11.053.References[1]N.G.Dhere,R.G.Dhere,J.Vacuum Sci.Technol.A23(2005)1208e1214.[2]J.Zhao,A.Wang,M.A.Green,Solar Energy Mater.Sol.Cells66(2001)27e36.[3]O.Schultz,S.W.Glunz,G.P.Willeke,Prog.Photovoltaics Res.Appl.12(2004)553e558.Fig. 4.Thickness profiles taken after TiO2sintering(blue line),after perovskite annealing(black line)and after P3HT drying(red line)over a c-TiO2/FTO/glass sub-strate.All measurements were taken on the same area of the same device,and the raw data were smoothed to remove noise.(For interpretation of the references to colour in thisfigure legend,the reader is referred to the web version of thisarticle.)Fig. 3.Current density e voltage(JV)curves of the best FTO/c-TiO2/nc-TiO2/CH3NH3PbI(3Àx)Cl x/P3HT/Au(red line and symbols)and FTO/c-TiO2/nc-TiO2/CH3NH3PbI(3Àx)Cl x/Spiro-OMeTAD/Au(black line and symbol)solar cells.(For inter-pretation of the references to colour in thisfigure legend,the reader is referred to theweb version of this article.)F.Di Giacomo et al./Journal of Power Sources251(2014)152e156155[4]G.Solar,2013/why-3g.[5]S.Hegedus,Prog.Photovoltaics Res.Appl.14(2006)393e411.[6] B.O’Regan,M.Grätzel,Nature353(1991)737e740.[7] A.Yella,H.-W.Lee,H.N.Tsao,C.Yi,A.K.Chandiran,M.K.Nazeeruddin,E.W.-G.Diau,C.-Y.Yeh,S.M.Zakeeruddin,M.Grätzel,Science334(2011)629e634.[8]M.I.Asghar,K.Miettunen,J.Halme,P.Vahermaa,M.Toivola,K.Aitola,P.Lund,Energy Environ.Sci.3(2010)418e426.[9]S.Mastroianni,nuti,S.Penna,A.Reale,T.M.Brown,A.Di Carlo,F.Decker,Chemphyschem13(2012)2925e2936.[10]I.K.Ding,N.Tétreault,J.Brillet, B.E.Hardin, E.H.Smith,S.J.Rosenthal,F.Sauvage,M.Grätzel,M.D.McGehee,Adv.Funct.Mater.19(2009)2431e2436.[11]W.Zhang,R.Zhu,F.Li,Q.Wang,B.Liu,J.Phys.Chem.C115(2011)7038e7043.[12] F.Matteocci,S.Casaluci,S.Razza,A.Guidobaldi,T.M.Brown,A.Reale,A.DiCarlo,J.Power Sources246(2014)361e364.[13]R.Søndergaard,M.Hösel,D.Angmo,rsen-Olsen, F.C.Krebs,Mater.Today15(2012)36e49.[14] E.L.Ratcliff,J.L.Jenkins,K.Nebesny,N.R.Armstrong,Chem.Mater.20(2008)5796e5806.[15]J.Melas-Kyriazi,I.K.Ding,A.Marchioro,A.Punzi,B.E.Hardin,G.F.Burkhard,N.Tétreault,M.Grätzel,J.-E.Moser,M.D.McGehee,Adv.Energy Mater.1 (2011)407e414.[16] F.Matteocci,G.Mincuzzi, F.Giordano, A.Capasso, E.Artuso, C.Barolo,G.Viscardi,T.M.Brown,A.Reale,A.Di Carlo,Org.Electron.14(2013)1882e1890.[17] E.Mosconi,A.Amat,M.K.Nazeeruddin,M.Grätzel,F.De Angelis,J.Phys.Chem.C117(2013)13902e13913.[18] A.Abrusci,S.D.Stranks,P.Docampo,H.-L.Yip,A.K.Y.Jen,H.J.Snaith,Nano Lett.13(2013)3124e3128.[19]J.M.Ball,M.M.Lee,A.Hey,H.J.Snaith,Energy Environ.Sci.6(2013)1739e1743.[20]J.H.Heo,S.H.Im,J.H.Noh,T.N.Mandal,C.S.Lim,J.A.Chang,Y.H.Lee,H.J.Kim,A.Sarkar,M.K.Nazeeruddin,M.Grätzel,S.I.Seok,Nat.Photonics7(2013)486e491.[21]J.Burschka,N.Pellet,S.-J.Moon,R.Humphry-Baker,P.Gao,M.K.Nazeeruddin,M.Grätzel,Nature499(2013)316e319.[22]M.Liu,M.B.Johnston,H.J.Snaith,Nature501(2013)395e398.[23] D.Bi,L.Yang,G.Boschloo,A.Hagfeldt,E.M.J.Johansson,J.Phys.Chem.Lett.4(2013)1532e1536.[24]M.M.Lee,J.Teuscher,T.Miyasaka,T.N.Murakami,H.J.Snaith,Science338(2012)643e647.[25]J.H.Noh,S.H.Im,J.H.Heo,T.N.Mandal,S.I.Seok,Nano Lett.13(2013)1764e1769.[26]V.Zardetto, F.Di Giacomo, D.Garcia-Alonso,W.Keuning,M.Creatore,C.Mazzuca,A.Reale,A.Di Carlo,T.M.Brown,Adv.Energy Mater.3(2013)1292e1298.[27]T.Zubkov,D.Stahl,T.L.Thompson,D.Panayotov,O.Diwald,J.T.Yates,J.Phys.Chem.B109(2005)15454e15462.[28]T.Leijtens,I.K.Ding,T.Giovenzana,J.T.Bloking,M.D.McGehee,A.Sellinger,ACS Nano6(2012)1455e1462.[29]H.Chen,X.Pan,W.Liu,M.Cai,D.Kou,Z.Huo,X.Fang,S.Dai,mun.49(2013)7277e7279.[30]H.-H.Liao,C.-M.Yang,C.-C.Liu,H.Sheng-Fu,M.Hsin-Fei,S.Jow-Tsong,J.Appl.Phys.103(2008)104506e104508.[31] C.-K.Lu,H.-F.Meng,Phys.Rev.B75(2007)235206.[32] A.Abrusci,S.D.Stranks,P.Docampo,H.-L.Yip,A.K.Y.Jen,H.J.Snaith,Nano Lett.(2013).[33]L.Yang,U.B.Cappel,E.L.Unger,M.Karlsson,K.M.Karlsson,E.Gabrielsson,L.Sun,G.Boschloo,A.Hagfeldt,E.M.J.Johansson,Phys.Chem.Chem.Phys.14 (2012)779e789.F.Di Giacomo et al./Journal of Power Sources251(2014)152e156 156。

High fidelity, high power switched amplifier

High fidelity, high power switched amplifier

专利名称:High fidelity, high power switched amplifier发明人:Juan Antonio Sabate,Richard S. Zhang,LuisJose Garces,Paul Michael Szczesny,QimingLi,William Frederick Wirth申请号:US10867598申请日:20040615公开号:US20050275404A1公开日:20051215专利内容由知识产权出版社提供专利附图:摘要:A gradient amplifier arrangement is described that comprises a gradientamplifier power stage. The device may be employed to provide a current to a gradientcoil, as in a MRI system. The circuitry disclosed includes a series coupling of a first bridge amplifier operating at a first voltage, a second bridge amplifier operating at a second voltage, a third bridge amplifier operating at a third voltage, and a gradient amplifier control stage. The amplifiers may provide output voltages at different levels, and may be switched at different times and frequencies to provide a range of output voltage and current levels.申请人:Juan Antonio Sabate,Richard S. Zhang,Luis Jose Garces,Paul Michael Szczesny,Qiming Li,William Frederick Wirth地址:Gansevoort NY US,Rexford NY US,Niskayuna NY US,Ballston Lake NYUS,Shanghai CN,Johnson Creek WI US国籍:US,US,US,US,CN,US更多信息请下载全文后查看。

HIGH EFFICIENCY POWER PRODUCTION METHODS, ASSEMBLI

HIGH EFFICIENCY POWER PRODUCTION METHODS, ASSEMBLI

专利名称:HIGH EFFICIENCY POWER PRODUCTION METHODS, ASSEMBLIES, AND SYSTEMS 发明人:PALMER, Miles R.,ALLAM, RodneyJohn,FETVEDT, Jeremy Eron申请号:EP11764638.0申请日:20110920公开号:EP2619418A1公开日:20130731专利内容由知识产权出版社提供摘要:The present disclosure provides methods, assemblies, and systems for power production that can allow for increased efficiency and lower cost components arising from the control, reduction, or elimination of turbine blade mechanical erosion by particulates or chemical erosion by gases in a combustion product flow. The methods, assemblies, and systems can include the use of turbine blades that operate with a blade velocity that is significantly reduced in relation to conventional turbines used in typical power production systems. The methods and systems also can make use of a recycled circulating fluid for transpiration protection of the turbine and/or other components. Further, recycled circulating fluid may be employed to provide cleaning materials to the turbine.申请人:Palmer Labs, LLC,8 Rivers Capital, LLC地址:300 Fuller Street Durham, North Carolina 27701 US,300 Fuller Street Durham, North Carolina 27701 US国籍:US,US代理机构:Hoeger, Stellrecht & Partner Patentanwälte 更多信息请下载全文后查看。

GaN-Based RF Power Devices and Amplifiers

GaN-Based RF Power Devices and Amplifiers

GaN-Based RF Power Devices and AmplifiersGallium nitride power transistors can operate at millimeter wave and beyond to meet future needs of cell phones,satellites,and TV broadcasting.By Umesh K.Mishra,Fellow IEEE,Likun Shen,Thomas E.Kazior,and Yi-Feng WuABSTRACT|The rapid development of the RF power electronics requires the introduction of wide bandgap mate-rial due to its potential in high output power density,high operation voltage and high input impedance.GaN-based RF power devices have made substantial progresses in the last decade.This paper attempts to review the latest develop-ments of the GaN HEMT technologies,including material growth,processing technologies,device epitaxial structures and MMIC designs,to achieve the state-of-the-art microwave and millimeter-wave performance.The reliability and manu-facturing challenges are also discussed.KEYWORDS|Gallium nitride;High Electron Mobility Transistors (HEMTs);microwave transistors;millimeter wave transistors; MMICs;reliabilityI.INTRODUCTIONWith the recent upsurge of the wireless communication market,as well as the steady but continuous progress of traditional military applications,microwave transistors are playing critical roles in many aspects of human activities. The requirements for the performance of microwave transistors are becoming more and more demanding.In the personal mobile communication applications,next generation cell phones require wider bandwidth and improved efficiency.The development of satellite com-munications and TV broadcasting requires amplifiers operating at higher frequencies(from C band to Ku band,further to Ka band)and higher power to reduce the antenna size of terminal users.The same requirement holds for broadband wireless internet connections as well because of the ever increasing speed or data transmission rate.Because of these needs,there has been significant investment in the development of high performance microwave transistors and amplifiers based on Si/SiGe, GaAs,SiC and GaN.Table1lists the major parameters of these materials and the Johnson’s figure of merit(JM) calculated to compare the power-frequency limits of different materials[1].The JM gives the power-frequency limit based solely on material properties and can be used to compare different materials for high frequency and high power applications.The requirement for high power and high frequency requires transistors based on semiconductor materials with both large breakdown voltage and high electron velocity. From this point of view,wide bandgap materials,like GaN and SiC,with higher JM are preferable.The wide bandgap results in higher breakdown voltages because the ultimate breakdown field is the field required for band-to-band impact ionization.Moreover,both have high electron saturation velocities,which allow high frequency opera-tion.The ability of GaN to form heterojunctions makes it superior compared to SiC,in spite of having similar breakdown fields and saturation electron velocities.GaN can be used to fabricate high electron mobility transistors (HEMTs)whereas SiC can only be used to fabricate metal semiconductor field effect transistors(MESFETs).The advantages of the HEMT include its high carrier concen-tration and its higher electron mobility due to reduced ionized impurity scattering.The combination of high carrier concentration and high electron mobility results in a high current density and a low channel resistance,which are especially important for high frequency operation and power switching applications.From the amplifier point of view,GaN-based HEMTs have many advantages over existing productionManuscript received February5,2007;revised August22,2007.U.K.Mishra and L.Shen are with the Department of Electrical and ComputerEngineering,University of California,Santa Barbara,CA93106USA(e-mail:mishra@;lkshen@).T.E.Kazior is with the Raytheon RF Components,Andover,MA01810USA(e-mail:Thomas_E_Kazior@).Y.-F.Wu is with the Santa Barbara Technology Center,CREE Inc.,Goleta,CA93117USA(e-mail:yifeng_wu@).Digital Object Identifier:10.1109/JPROC.2007.911060Vol.96,No.2,February2008|Proceedings of the IEEE287 0018-9219/$25.00Ó2007IEEEtechnologies (e.g.GaAs)[2].The high output power density allows the fabrication of much smaller size devices with the same output power.Higher impedance due to the smaller size allows for easier and lower loss matching in amplifiers.The operation at high voltage due to its high breakdown electric field not only reduces the need for voltage conversion,but also provides the potential to obtain high efficiency,which is a critical parameter for amplifiers.The wide bandgap also enables it to operate at high temperatures.At the same time,the HEMT offers better noise performance than that of MESFET’s.These attractive features in amplifier applications enabled by the superior semiconductor properties make the GaN-based HEMT a very promising candidate for microwave power applications.In this article we discuss the key components of GaN HEMT technology.In Section II we review growth of high purity device layers by metal organic chemical vapor deposition (MOCVD)and molecular beam epitaxy (MBE).In Section III we present device engineering and processing technologies that are being developed to realize state-of-the-art GaN HEMT performance.The reliability and manufacturing challenges are also discussed.In Section IV,we highlight some of the GaN HEMT hybrid amplifiers and monolithic microwave integrated circuit (MMIC)that have recently been achieved.II.GaN EPITAXIAL LAYER GROWTHNumerous teams have been developing the MOCVD and MBE techniques for growth of group-III nitride materials such as GaN,AlN,AlGaN,and InGaN [3]–[8].In the MOCVD process,Ga,Al,and In are supplied using corresponding metal organic compounds,usually tri-methylgallium,trimethylaluminum and timethylindium.The metal-organic compounds are then transported by a carrier gas,most often hydrogen.Thereby the concentra-tion of the compound in the carrier gas is determined by its vapor pressure.The most commonly used nitrogen source is ammonia.In the RF-MBE technique reactive nitrogen atoms and molecules are produced by passing a nitrogen flow (N 2gas)through a plasma discharge.A variant of this process uses ammonia ðNH 3Þas the nitrogen source gas[8].The column III growth fluxes are provided by evaporation of high purity elemental sources.The growth efforts of both techniques have been focused on developing high power microwave and millimeter-wave AlGaN/GaN HEMT structures.SiC has been extensively employed as substrates due to its excellent thermal conductivity [9],while sapphire and Si are also used because of the low cost [10],[11].Device isolation from the SiC and Si substrate is provided by a resistive AlN nucleation layer,in which the growth conditions are adjusted to prevent silicon out diffusion [12].Excellent material quality has been achieved for GaN HEMT films.The impurity concentrations in semi-insulating GaN films are below the detection limit when characterized by SIMS.AlGaN/GaN,AlN/GaN [13],GaN/AlN/GaN [14]and AlGaN/AlN/GaN [15]heterostructures with smooth and abrupt interfaces have been demonstrat-ed,leading to the formation of 2DEGs with electron mobilities as high as 2000cm 2=Vs at room temperature [16].Non-uniformites of G 2%on 4-inch diameter SiC substrates are routinely achieved (for example,see Fig.1(a)V a sheet resistivity map of a GaN DHFET (Double Heterostructure Field-Effect Transistors)[17].Mercury probe capacitance-voltage (C-V)measure-ments of AlGaN/GaN HEMT structures grown on semi-insulating SiC substrates reveal high quality material.The C-V profile exhibits a sharp pinch-off and extremely low,flat capacitance at high reverse bias (equal to the capacitance of the SiC substrate)indicative of negligible GaN buffer and epi/SiC interface charge/doping [as shown in Fig.1(b)][18].Both MOCVD and MBE techniques are capable ofgrowing thin layers.The use of a thin,$10A˚,AlN interlayer between the AlGaN barrier and GaN channel has been demonstrated to reduce sheet resistance by increasing the mobility and sheet density of the HEMT structure [15].The increase in mobility is attributed to the reduction in alloy scattering and the increase in sheet charge due to the larger conduction band discontinuity at the AlGaN/GaN interface.Fig.2is an x-ray spectrum of a250A˚Al 0:26Ga 0:74N =10A ˚AlN/GaN HEMT grown on a SiC substrate.The presence of the thin,AlN layer enhances the strength of the Pendellosung oscillations.Table 1Material Properties Related to the Power Performance at High Frequencies for VariousMaterialsMishra et al.:GaN-Based RF Power Devices and Amplifiers288Proceedings of the IEEE |Vol.96,No.2,February 2008(The Pendellosung oscillations are a measure of the quality (flatness and abruptness)of the hetero-interface.)The AlN interlayer lowered the sheet resistance from 400to 285ohm/sq.and the mobility was increased to greater than 2000cm 2=Vs.Using the MOCVD and MBE techniques,growers have demonstrated more complex device structures similar to GaAs pHEMTs,such as quantum well or double hetero-junction (DH)FETs.Some of these devices operate up to W-band frequencies.The quantum well or DH structures provide improved electron confinement to mitigate short channel effects associated with smaller gate lengths as wellas better substrate isolation resulting in higher gain devices and improved device efficiency.AlGaN buffer layers [19]and InGaN backside barrier layers [20]–[22]have been used to create conduction band discontinuities (double quantum wells similar to GaAs pHEMTs and InP HEMTs)that inhibit the injection of electrons into the buffer layer.Improved channel confinement/buffer iso-lation and reduced buffer leakage current by Fe,Be,or C doping of the GaN buffer layer (similar to fully depleted buried p-layers commonly used in GaAs MESFETs and Si nMOS devices)has also been demonstrated [23]–[26].Finally,highly doped cap layers are being added to the epi structure to reduce device access (source)resistance,which results in increased device gain and efficiency [19],[27].III.ADVANCED DEVICE DESIGNS AND PROCESSING TECHNOLOGIESWhile several electronic devices have been investigated (for example,HBTs [28],MESFETs [29],MISFETs [30],HEMTs [31]),most of the research work has been focused on HEMTs [including MOSHEMT [32](Metal-oxide-semiconductor HEMT)],because HEMTs have better carrier transport properties than MESFETs and the difficulty of p-doping in GaN impedes the development of bipolar transistors.A typical AlGaN/GaN HEMT is shown in Fig.3.The polarization doping effect in GaN HEMTs was predicted by Bykhovski et al.[33].The first observation of a Two-Dimensional Electron Gas (2DEG)with a carrier concentration of the order of 1011cm À2and a room temperature mobility of 400–800cm 2=Vs in an AlGaN/GaN heterojunction was reported in 1992[31].ThefirstFig.1.(a)Sheet resistance map and (b)capacitance-voltage plot for GaN HEMT grown on a 4-inch SiCsubstrate.DC performance of AlGaN/GaN HEMT was shown in 1993with the saturation drain current of 40mA/mm [34].First RF power data of 1.1W/mm at 2GHz for an AlGaN/GaN HEMT was demonstrated in 1996[35].In the early stage of the development of the GaN devices,many AlGaN/GaN HEMTs suffered a discrepancy between the predicted output power from static I-V curves and load pull measurements of output power,referred to as B DC-to-RF dispersion.[As seen in Fig.4,current collapse occurs in the pulsed I-V measurement.It is believed to be a trap-related phenomenon where both surface and bulk traps contribute [36],[37].The existence of the dispersion has severely limited the microwave output power of GaN HEMTs,until two innovations were proposed to overcome this problem.One was the introduction of the Si x N passivation in 2000[38],[39],which effectively reduced DC-to-RF dispersion caused by surface trap states,thereby resulting in a significant increase in output power to 9and 11W/mm [40],[41].Another was the adoption of the field plate in 2003[10],[42].In addition to the traditional function of the field plate to increase the breakdownvoltage,it also reduced the dispersion beyond what Si x N passivation offered.Since then,the output power density has further increased with the help of steadily improved growth techniques,material qualities,enhanced proces-sing technologies and more optimum device designs.The latest record for power density is over 40W/mm at 4GHz [43].The trend of the GaN-based device is towards higher output power density,higher Power-Added-Efficiency (PAE),higher operation frequencies and improved reli-ability.In order to achieve these requirements,novel device designs and processing technologies are being developed.Recently,much progress has been made and will be discussed below.The first subsections focus on improvements to the performance of microwave transis-tors.The last subsection addresses the unique challenges of optimizing the device for millimeter wave applications.A.Field-Plated GaN HEMTsImplementing a field plate on a dielectric layer at the drain side of the GaN HEMTs has resulted in some of the most significant and exciting improvements [10],[42],[43].The performance and tradeoffs of the field plate (FP)configurations have been investigated in an attempt to extract the best gain and power characteristics.Gate Connected FP (GC-FP):Fig.5(a)shows the cross section of a gate-connected field-plated GaN HEMT.The function of a FP is to modify the electric field profile and to decrease its peak value,hence reducing trapping effect and increasing breakdown voltages.Initial FPs were either constructed as part of the gate or tied to the gate externally.This has been effective in improving large signal (or power)performance and enabling high voltage operation as seen in Fig.6(a)and (b)[44].Up to a certain value,the longer the FP,the more output power was achieved.However,in this configuration the capacitance be-tween the FP and drain becomes gate-to-drain capacitance ðC gd Þ,resulting in negative Miller feedback.This causes reduction in current-gain and power-gain cutoff frequen-cies ðf t =f max Þas seen in Fig.7.Source-Connected FP (SC-FP):A close look into the device operation reveals that,since the voltage swing across the gate and source is only 4–8V for a typical GaN HEMT,much less than the dynamic output swing up to 230V,terminating the FP to the source [shown in Fig.5(b)]also satisfies the electrostatics for it to be functional.In this configuration,the FP-to-channel capacitance becomes the drain-source capacitance,which could be absorbed in the output-tuning network.The drawback of additional C gd by the FP is hence is eliminated.Depending on the implementation,the source-connected field plate can add parasitic capacitance to the device input.However,this can also beabsorbedFig.3.A schematic of a typical AlGaN/GaNHEMT.Fig.4.DC and pulsed I-V characteristics of an unpassivated AlGaN/GaNHEMT on SiC substrate.Obvious current collapse (dispersion)could be observed in the pulsed mode.Mishra et al.:GaN-Based RF Power Devices and Amplifiers290Proceedings of the IEEE |Vol.96,No.2,February 2008into the input tuning circuit,at least for narrow band applications.SC-FP,GC-FP and non-FP Devices were fabricated on the same wafer for a direct pared to the non-FP device,the reveres power transferðS12Þof the device with GC-FP increased by71%at4GHz,while that of the device with SC-FP actually reduced by28%.The reduction in S12for the latter is attributed to the Faraday shielding effect by the grounded field plate.As a result, at10V drain bias and4GHz the SC-FP device exhibited a maximum-stable-gain(MSG)1.3-dB higher than the non-FP device and5.2dB higher than the GC-FP device. As a result,the SC-FP devices shows a significant(95dB at4GHz)improvement in maximum stable gain,This advantage for SC-FP devices was maintained for biases from10though60V as seen in Fig.8(a).Fig.8(b)lists the change of the capacitance components in GC-and SC-FP devices,respectively.Large-signal performance was characterized by load-pull power measurement at4GHz.Both the GC-FP and the SC-PF devices outperformed the non-FP devices in both output power and PAE at48V and above,while the SC-FP device consistently delivered large-signal gains 5–7dB higher than that of the GC-FP device.As successful high-voltage designs,both FP devices were able to operate at118V dc bias as shown in Fig.9, where tuning was optimized for the best combination of gain,power-added-efficiency(PAE)and output powerat Fig.5.Cross section of a GaN HEMT with(a)gate-connected field plate;(b)source-connected fieldplate.Fig.6.(a)Power density vs.drain voltage for various FP lengths.Device dimension:0:5Â246 m2.(b)Power performance of aGaN HEMTs with gate-connected field plates,showing32.2W/mm output power at120V drain bias.Mishra et al.:GaN-Based RF Power Devices and AmplifiersVol.96,No.2,February2008|Proceedings of the IEEE2913-dB compressionðP3dBÞ.While both devices generate power densities around20W/mm,the SC-FP device distinguishes itself by7-dB higher associated gain.With the achieved large-signal gain of21dB at4GHz and the estimated voltage swing of224V,the voltage-frequency-gain product(Johnson’s voltage-frequency figure of merit [1])for the SC-FP is approaching10kV-GHz,the highest ever shown for any semiconductor device.The above studies were for operation at C-band and below.For applications at X-band and above,dimensions for the field plates need to be reduced accordingly to manage the parasitic capacitances.B.Deep-Recessed GaN HEMTsSiN x passivation has been used to reduce the disper-sion,but reproducibility of breakdown voltage,gate leakage,and effectiveness of dispersion elimination is strongly process related.Recently,solutions to the dispersion problem had been addressed at the epitaxial level[45],[46].One of these approaches,which has made substantial progress,is the deep-recessed GaN HEMT using a thick cap layer to eliminate dispersion[47],as shown in Fig.10.The effect of the surface to the channel is inversely proportional to the distance between surface and channel. The thick AlGaN or GaN cap layers in the deep-recessed HEMTs increase the surface-to-channel distance,the dispersion caused by surface traps is therefore reduced or eliminated without surface passivation because now only a smaller portion of the channel charge is affected compared to the conventional AlGaN/GaN HEMTs.The graded AlGaN layer is Si-doped to compensate the negative polarization charge and prevent hole accumulation.The processing flow was similar to that of the standard HEMT except for the deep ohmic and gate recess.A fluorine plasma treatment of the recessed surface before gate metallization was found to be very effective to reduce the gate leakage(up to two orders of magnitude)and increase breakdown voltage(9200V)[48].A record output power density P out of more than17W/mm with an associated power added efficiency(PAE)of50%was measured at V DS¼80V at4GHz(without SiN x passivation as shown in Fig.11).This is believed to be the highest power generated from a GaN transistor with-out surface passivation to date.At lower bias of30V, an excellent PAE of74%with output power density of 5.5W/mm was achieved.In order to control the recess depth accurately and improve the manufacturability,a selective dry etch tech-nology of GaN over AlGaN using BCl3=SF6has been developed[49].The presence of fluorine decreases the etch rate of AlGaN due to the formation of anon-volatile Fig.7.f t=f max as functions of FP length L f.Fig.8.(a)MSG as a function of drain voltage;(b)change of the capacitance components in GC-and SC-FP devices.Mishra et al.:GaN-Based RF Power Devices and Amplifiers292Proceedings of the IEEE|Vol.96,No.2,February2008AlF 3residue on the AlGaN surface.The compatible deep-recessed structure has a GaN cap (9200nm)and an abrupt GaN/AlGaN interface to clearly define the etch-stop position,seen in Fig.12.Selectivity of around 25of GaN over Al 0:22Ga 0:78N was achieved.The selectivity increased with Al composition in AlGaN,up to about 50–100between GaN and AlN.The devices processed with selective etch technology demonstrated significantly reduced processing variations as well as excellent microwave power performance.At 10GHz,a high PAE of 63%with an output power density of 5W/mm was achieved at V D ¼28V,while 10.5W/mm with 53%PAE was achieved at V D ¼48V,shown in Fig.13.The power performance of these devices with gate length of 0.6 m is comparable to state-of-the-art conventional SiN x -passivated AlGaN/GaN HEMTs at 10GHz.C.Metal-Oxide-Semiconductor HEMT (MOSHEMT)The MOSHEMT design combines the advantages of the MOS structure,which suppresses the gate-leakage current,and an AlGaN/GaN heterointerface that provides high-density high-mobility 2DEG channel [50].The MOSHEMT approach also allows for application of high positive gate voltages to further increase the sheet electron density in the 2-D channel and,therefore,the peak device current.The MOSHEMT built-in channel is formed by the high-density 2DEG at the AlGaN/GaN interface as in regular AlGaN/GaN HEMTs.However,in contrast to a regular HEMT,the gate metal is isolated from the AlGaN barrier layer by a thin dielectric film such as SiO 2,AlO,ZrO,NbO,AlN,HfO2and so on,as seen in Fig.14.Thus,the MOSHEMT gate behaves more like a MOS gate structure rather than a Schottky barrier gate used in regular HEMTs.Since the properly designed AlGaN barrier layer is fully depleted by electron transfer to the adjacent GaN layer,the gate insulator in the MOSHEMT consists of two sequential layers:the SiO 2film and AlGaN epilayer.This double layer ensures an extremely low gate-leakage current and allows for a large negative to positive gate voltage swing.The suppression of the gate-leakage current is one of the most important features of the MOSHEMT.In Fig.15,the gate-leakage currents for the 1:5 m Â200 m gate MOSHEMT at different temperatures is shown.The data shows that the MOSHEMT leakage current is as low as 1nA/mm at 20-V gate bias at room temperature and is approximately six orders of magnitude smaller than for the regular HEMT with similargateFig.9.Power sweeps with a SC-FP device and a GC-FP device at 118V drain bias and 4GHz.Device dimension:0:5Â500 m 2.Fig.10.Device structure of a deep-recessed GaN HEMT with AlGaN cap.Mishra et al.:GaN-Based RF Power Devices and AmplifiersVol.96,No.2,February 2008|Proceedings of the IEEE293dimensions.Even at 300 C,the gate-leakage current for MOSHFET remains 3–4orders of magnitude lower than for regular HEMTs.The maximum DC saturation drain current at positive gate voltages is a key parameter controlling maximum output RF power.For conventional AlGaN/GaN HEMTs,gate voltages in excess of 1.2V result in excessive forward current.In a MOSHEMT,the gate voltages as high as 10V could be applied.This results in significant increase in maximum channel current.The gate leakage,however,remains well below 1nA/mm.Fig.16shows the transfer characteristics for the 1.5 m-gate-length MOSHEMT and HEMT measured at the drain voltage sufficient to shift the operating point into the saturation regime.With the Si x N surface passivation and field plate,the MOSHEMT demonstrated an output power density of 18.6W/mm with a PAE of 49.5%at drain bias of 55V at 2GHz,seen in Fig.17.Moreover,there was no degra-dation after the RF-stress at such a high output power density for 100hours [51].The application of the MOSHEMT to higher frequencies (e.g.26GHz)has also been demonstrated [52].The gate leakage was muchlower and the maximum output power was 3dB higher than a HEMT fabricated by the same group.A more careful scaling of the gate length and gate oxide thickness,or adoption of high-K dielectrics,could extend the MOSHEMT into the millimeter-wave frequencies.D.Process and Device Technology for GaN HEMTs for mm-Wave ApplicationsNew applications are demanding high output power and efficiency at higher frequencies,especially Ka-band (26–40GHz)and beyond,with the aim to replace or complement traveling wave tube amplifiers.Satellite and broad-band wireless communications as well as advanced radars are only a few of the many applications that would greatly benefit from the increased reliability,reduced size and noise of these solid-state based amplifiers.In order to achieve the goal of working at mm-Wave frequencies and beyond,new process technologies and device structures have to be utilized.The gate-to-source spacing of mm-Wave HEMT must be minimized,to keep the source access resistancelow.Fig.11.Power performance at 4GHz without SiN xpassivation.Fig.12.Device structure of a deep-recessed GaN HEMT with GaN cap,which is compatible with selective etchtechnology.Fig.13.Power performance at 10GHz without Si x Npassivation.However,the conventional alloyed ohmic contacts have rough morphology and edges,which limits the reduction of the gate-to-source spacing.Therefore,a non-alloyed ohmic contact is preferred for the high frequency devices.Ion implantation has been used in the GaN device fabrication to form non-alloyed ohmic contacts [53],[54].In the past,a high temperature ð1200$1500 C Þannealing process was employed using protective surface layers during the implant activation annealing including SiO 2[55],Si 3N 4[56]and AlN [54],as well as high pressure ($100bar N 2).However,the use of a high temperature,high pressure and capped annealing processes limits the manufacturability of this process for AlGaN/GaN HEMTs.Recently investiga-tors began applying this technique to selectively Si dope the source and drain contact region of the GaN HEMT in order to reduce the contact resistance and enable the creation of non-alloyed ohmic contacts (see Fig.18)[57].The non-alloyed ohmic contacts formed on the implanted region have much smoother surfaces than alloyed contacts,as shown in Fig.19.The smooth edges of the ohmic contacts allow the reduction of the gate-drain spacing,thus further lowering the access resistance,which is important to high frequency devices.The same investigators have also demonstrated a capless implant activation anneal with a reduced thermal budget and improved the manufactur-ability [57].Devices fabricated with the non-alloyed ohmic con-tacts exhibit performance comparable to control devices,indicating that the implant and capless anneal process do not degrade the HEMT material characteristics.Re-cently,a non-alloyed ohmic contact resistance lower than 0.3 –mm was achieved with the optimization of the ion implantation process including reduction of the spacing between the implant and ohmic edge.The HEMT showed an excellent PAE of 60%with an output power density of 7.3W/mm at 10GHz when V D ¼35V [58].In the past few years,the power performance at Ka-band has made steady progress.For instance,an output power density of 2.8W/mm was reported at 40GHz in 2003[59]and 5.7W/mm at 30GHz in 2004[60].Fig.15.Gate-leakage currents for the MOSHEMT 1:5 m Â200 mgate at different temperatures and the baseline HEMT at room temperature measured in diode mode (draindisconnected).Fig.17.Power sweep at 2GHz for a 200- m-wide device.Devicedimensions are L sd ¼6 m,L g ¼1:1 m,L FP ¼2:1 m with a 1.1- m overlap with thegate.Recently,an output power of 10.5W/mm with a PAE of 34%was demonstrated at 40GHz at drain bias of 30V,as shown in Fig.20[61].The device had a gate length of 160nm and showed a current gain cut-off frequency ðf T Þof 70GHz and a maximum power gain cut-off frequency ðf max Þof 100GHz.The very high output power is the result of the combination of both very high current densities ($1.4A/mm at V GS ¼þ2V)and breakdown voltages (980V)with negligible knee walk-out and current collapse.Higher f T and f max are required for operation beyond Ka-band and are attracting much research efforts [62].The traditional methods,for instance,shorter gate length,multiple fingers to reduce gate resistance and À-shaped gate to decrease gate-to-drain capacitance,are still effective to further boost the device performance.A f T of 180GHz has been achieved with 30-nm-gate,thin AlGaN barrier layer and CAT-CVD-deposited SiN thin layer [63].In order to improve the confinement of the electrons to reduce the output conductance and improve f max ,the concept of the back-barrier has attracted some research recently.The DHFET utilizing a low Al contentAl 0:04Ga 0:96N buffer achieved three orders of magnitude lower sub-threshold drain leakage and demonstrated 30%improvement in output density and 10%improvement in PAE [64].Another InGaN back-barrier design used the unique strong polarization property of GaN to improve the channel charge confinement [65].The sample structure was shown in Fig.21.The ultra-thin InGaN layer is 1nm thick and has an In composition of 10%.As shown in Fig.22(b),the pinch-off characteristics of the sample with an InGaN back-barrier are excellent for drain voltages as high as 50V,much better than the control sample without InGaN back-barrier [Fig.22(a)].This led to an improvement ofoutputFig.19.(a)Rough surface morphology of the alloyed ohmic contactof GaN HEMTs (b)smooth surface morphology of the nonalloyed ohmiccontact.Fig.20.Power sweep of a mm-wave MOCVD AlGaN/GaN HEMTshowing a maximum power of 10.5W/mm and PAE of 33%at 40GHz.The drain voltage was 30V and the drain bias current was 500mA/mm.Fig.21.Schematic and band diagram of the InGaN back-barriersample.Mishra et al.:GaN-Based RF Power Devices and Amplifiers296Proceedings of the IEEE |Vol.96,No.2,February 2008。

Review of high power density superconducor

Review of high power density superconducor

Review of high power density superconducting generators:Presentstate and prospects for incorporating YBCO windingsPaul N.Barnesa,*,Michael D.Sumption b ,Gregory L.RhoadsaaPropulsion Directorate,Air Force Research Laboratory,Bldg 450,2645Fifth Street,Wright-Patterson AFB,OH 45433,USAbDepartment of Materials Science and Engineering,Ohio State University,Columbus,OH 43210,USAAbstractThis work focuses on the development of high power density generators for airborne applications by bridging the chasm between generator and high temperature superconducting (HTS)wire developmental efforts.Benefits of HTS power generation include improved efficiency,thermal management reduction,improved power handling,reduced life cycle costs,and size and weight reduction.Supercon-ducting generator development from the 1970s is outlined,and the basic types of ac synchronous generators are described.The benefits of HTS conductors in general and HTS coated conductors in particular are discussed.Critical issues for the employment of HTS coated conductors are then considered and recommendations made for enhancements to the HTS coated conductor for implementation in the more advanced superconducting power generators.Published by Elsevier Ltd.Keywords:High T c superconductors;YBCO coated conductor;Rotating electric machinery;Superconducting generators;Superconducting tapes1.Background1.1.The need and niche for high power density generators A variety of future military systems will depend on high electrical power input at the multimegawatt level.As is typ-ical for airborne,seaborne,and ground-mobile platforms,the power generation subsystems must often be packaged in a limited space and within strict weight limits.Conven-tional generators that provide high electrical power have been developed and optimized over the past several dec-ades,but these generators cannot provide the multimega-watt levels of power necessary for advanced mobile or airborne military systems without paying a significant pen-alty in size,weight,and efficiency.Efficiency,thermal man-agement,and fatigue life are typically sacrificed as conventional generators are given high rotational speedsto reduce their size and weight while maintaining the high power output.Thermal management dictates that as the re-quired power increases to megawatt levels,simple scaling of conventional airborne power generators is not a plausi-ble solution.The development of more efficient airborne generators is of critical importance.While the systems that use this power are being intensely developed,the greater power needed to make these systems function is often assumed.Only proactive efforts on novel power systems such as HTS generators will address these concerns.Below we will review some of the past technical accomplishments in the development of LTS-based generators.Several fundamen-tal roadblocks prevented widespread incorporation of these machines.HTS conductors can allow these limits to be cir-cumvented,however,HTS conductors may have their own set of difficulties to be addressed.In order to enable the successful development of high power density generators and their widespread usage,both a critical review of LTS-based generators and an assessment of relevant issues for HTS conductors are needed.We will start by outlining0011-2275/$-see front matter Published by Elsevier Ltd.doi:10.1016/j.cryogenics.2005.09.001*Corresponding author.Tel.:+19372554410;fax:+19376564095.E-mail address:paul.barnes@ (P.N.Barnes)./locate/cryogenicsCryogenics 45(2005)670–686the application niche for near-term military and govern-mental use of such generators,which may occur before large-scale commercial uses are feasible.Perhaps the earliest use for the superconducting techno-logies will be non-lethal weapons.Future military applica-tions will likely broaden the range of situations in which military force can be used as afirst strike option with non-lethal technologies.One specific technology being developed for such situations is Active Denial Technology (ADT)[1].ADT is a non-lethal directed energy weapon (DEW)which employs high power electromagnetic radia-tion.To make this system airborne will require the benefits of superconducting generators[2].Also,the required gyro-tron magnet is made with LTS.If this magnet could be re-placed with HTS conductor operating at60–77K(as opposed to4.2K)it would result in a significant reduction in weight,size,and electrical power requirements of the associated cryocooler.There are other applications for the US Air Force, Navy,and Army requiring large amounts of power.The US Air Force is also considering airborne DEW such as the Airborne Tactical Laser(ATL).Even chemically driven directed energy weapons such as the ATL will require greater electrical power to pump the chemicals through the laser.Similarly,the Army has a technological need for compact,lightweight power systems for DEW applica-tions on mobile platforms such as Ground Tactical Lasers. Development is also ongoing with both homopolar and synchronous superconducting motors to drive the US NavyÕs future all-electric ship[3].HTS wire technology can be used in many of the system components for these military applications such as motors,power generators, transformers,power converters/inductors,primary power cabling,and highfield magnets.Technologies such as electromagnetic launch or railguns require pulsed power[4],but often overlooked is the fact that the required average power of these application may extend into the megawatt range.This would require a con-tinuous electrical power generation system to charge the energy storage system,whether capacitor banks,pulse forming networks,etc.[5]as an alternative to pulsed mand and control operations are also demand-ing more power such as with the E-10A Multi-Mission Command and Control aircraft(MC2A).The MC2A would be capable of serving as an intelligence,surveillance and reconnaissance platform with a broader range of capa-bilities in a single package.Another potential application is in the arena of Home-land Defense.It is clear that commercial airports,power utility generation,and power distribution grids are vulner-able to terrorist attack.Solutions to counter these possible attacks would make use of small multimegawatt turbogen-erators which can be permanently located or rapidly de-ployed to these areas in the event of an attack.In the case of airports,a highly mobile superconducting power generation system could be employed to power advanced protective measures.For the transmission grid,these mobile high power generators can be deployed to critical nodes if power is disrupted.The system could simply be an aeroderivative turboshaft engine coupled to a HTS gen-erator to produce the required megawatts of power;the system could be contained in a trailer for transport to its needed location.In this work,we will aim to discuss the nature of this newer class of superconducting generators that is being developed to meet the needs outlined above and some of the requirements for incorporation of the HTS coated con-ductor.The intent is to establish a bridge between the development of these two technologies.HTS generators will use superconducting windings which maintain high efficiency(and thus lessen thermal management require-ments)and at the same time more critically reduce the ma-chine size and weight.This paper will focus in particular on the superconducting ac synchronous generator work espe-cially relevant to the US Air Force,and the roadblocks and possibilities associated with HTS conductor use.1.2.The need for superconducting windingsThe primary commercial application of superconducting generators will be in power utility facilities,either as new acquisitions or as retrofitted generators.Benefits of com-mercial HTS generators include energy savings,reduced pollution per unit of energy produced,lower life-cycle costs,enhanced grid stability,and reduced capital cost and installation expenses.The greatest incentives for the development of HTS generators are in the commercial sec-tor as opposed to the military due to the significantly larger market for power utility applications.However,govern-mental agencies are expected to be a driver in the develop-ment of this technology in the near term,because they represent an enabling technology for some military sys-tems.Below we review some of the specific reasons for using superconducting wire,especially HTS.1.2.1.Increased efficiency and thermal managementThe lack of dc resistance in superconducting wire virtu-ally eliminates ohmic heating in thefield windings of gener-ators.Superconducting generators can increase machine efficiency beyond99%,reducing losses by as much as 50%when compared to conventional generators.For air-borne generators,the increase in efficiency is even larger, by several percent.In fact,efficiency per se is not the main benefit here,more important is the fact that the improved efficiency significantly lessens the thermal management burden.At the lower overall power levels currently used in airborne applications today,the amount of waste heat does not pose a great problem.However,as power levels are increased to the megawatt level,the thermal manage-ment load becomes a non-neglible factor in the design of airborne generators.For example,if5MW of power is produced at85%efficiency,then750kW of heat must be either dumped off-board the aircraft or absorbed by the fuel.P.N.Barnes et al./Cryogenics45(2005)670–6866711.2.2.Size and weight reductionInitial commercial,HTS-based generators are expected to be a third or less of the overall volume of their conven-tional equivalents and one-half or less of their weight.In-deed,superconducting synchronous motors have already demonstrated reductions of this level[6].This reduction factor included the cryogenic refrigeration system and no special effort was taken to reduce its size.Less supercon-ducting wire is needed compared to copper in order to ob-tain the same magneticfield.Furthermore,the magnetic fields produced by the superconductor winding are high en-ough that no iron is needed to direct thefield lines(depend-ing on the particular generator configuration),which also means that the rotor-producedfields are not limited by the saturation characteristics of iron.This lack of iron also eliminates the losses experienced in the armature teeth. Superconducting generators built without iron in the rotor or stator and are referred to as‘‘air core’’designs;this fact also contributes to the weight savings versus conventional copper wound generators.Such designs are of particular interest to the US Air Force,although usage of iron,if min-imized,can still pose a viable solution.Incorporating these elements into the design and increasing the rotor speeds to greater than10,000rpm,as is typical in airborne genera-tors,a total reduction of$80%is achievable in size and weight for the generator itself.1.2.3.Enhanced power grid performanceAnother benefit of superconducting generators is related to its incorporation into the overall power grid.These advantages are more applicable for usages at bases and installations as opposed to mobile systems.The associated advantages include steady state and transient stability,such as a greater tolerance of negative sequencefields,an im-proved reactive power capability,and a potential increase of up to$30%in the power transfer limits of the transmis-sion system[7].One particular generator design had a low synchronous reactance,although the transient and sub-transient reactances are close to conventional values[8]. For HTS generators,a reduction in the amount of spinning reserve(unused but rotating generating capacity)is needed to ensure a stable overall power system[9].It is also ex-pected that an HTS generator has the capability of being significantly overexcited to permit power factor correction without adding synchronous reactors or capacitors to the power system[9].1.2.4.Low life-cycle costsIf the reliability and maintenance of a superconducting generator are comparable to present systems,it is expected that a reduction in life-cycle costs can be possible.Since superconducting generators are smaller and lighter than their conventional counterparts with the same power rat-ing,capital costs,shipping fees,and installation expenses can potentially be less,especially as the power output of the generator is increased.Superconducting generators can also offer a longer operating lifetime than conventional machines since conventional windings generally experience insulation degradation resulting from thermal aging.Cryo-genic applications can retard this degradation and the insu-lation of HTS generatorfield windings should last longer and not require the standard rewinding maintenance.An added environmental benefit of using superconducting wire for generators is a reduction in oil consumption[7].2.Introduction to superconducting synchronous generators ponentsSuperconducting ac synchronous generators work by electromagnetic induction;all rotating electric machines provide power based on FaradayÕs law.The ac voltages generated are the result of an induced electromotive force resulting from time varying magneticfields.In a generator, this is accomplished by motion between the armature wind-ing and the magneticfield windings(rotor coils or excita-tion coils).Either the armature windings are rotated within thefield produced by the excitation coils or vice ver-sa.When the excitation coils are rotated,they are referred to as the rotor;the stationary armature is then called the stator.Superconducting generators usually incorporate the superconducting wire into the rotorfield windings while retaining a non-cryogenic armature which employs standard copper windings.One approach for creating a power subsystem is to con-figure a prime power unit(PPU)with a combustion turbine engine that drives directly(without a gear box)a high speed superconducting synchronous generator.The cryo-genic sections of the synchronous generator would be cooled by an efficient and reliable mechanical refrigerator. Fig.1shows a typical power system layout for a supercon-ducting generator mated to a gas turbine.The Power Man-agement and Distribution(PMAD)scheme is dependent on the load.For example,a high voltage load might have a transformer as part of the PMAD.On the other hand, a low voltage load PMAD might use dc-to-dc power con-verters.The synchronous superconducting generator can be divided into three major subcomponents:the rotor, the stator,and the cooling system(Fig.2).The cooling sys-tem is generally stationary requiring cryogenic cooling lines connecting to the spinning rotor.On airborne generators with high rpm,the HTS coils in the rotor will experience large centrifugal forces.2.2.Hybrid vs all-cryogenic designsBasic synchronous superconducting generators can be sub-classified into two primary types.Thefirst is the classic (or hybrid)superconducting generator.This is the primary design that has been used to-date in which only the rotor windings use superconductors.The stator has a conven-tional design using copper windings except for the elimina-tion of the iron.In the rotor windings,the superconductor will generally experience a dcfield,thus ac losses are kept672P.N.Barnes et al./Cryogenics45(2005)670–686to a minimum and largely due to asynchronous feed back.Efficiencies of the structure are high since the superconduc-tor has zero dc resistance.However,there are issues associ-ated with isolating the rotating cryogenic vessel from the room temperature stator and the required cryogenic cool-ing connections to the spinning rotor.The other class of superconducting generators is the all-cryogenic or fully superconducting generator.In this case,both the rotor and stator windings are made of supercon-ducting material and the entire generator resides in a cryo-genic jacket.The armature windings will experience significant ac losses due to the rotating magnetic fields of the rotor.These ac losses will include hysteretic losses in the superconductor,normal metal effects such as eddy cur-rents,ferromagnetic substrate contributions,and coupling current losses.Successful incorporation of HTS conductor into the armature will require the additional development of an ac-tolerant YBCO coated conductor that will suffi-ciently minimize these effects.Until such time,hybrid superconducting generators will be the workhorse for superconducting power systems.Ultimately,however,an all-cryogenic design is the ideal for lightweight superconducting generators.This type of superconducting generator has a much simpler design and potential for high reliability.The weight improvement resulting from ac-tolerant YBCO stator coils is perhaps not the dominant factor in that the real benefits of the all-cryo-genic machine will be in manufacturability,reliability,and affordability in comparison with other types of lightweight generators.The all-cryogenic approach can potentially double the power density of the classical superconducting generator—one with HTS rotor only.3.Development of superconducting generators to date In establishing new programs for the development of superconducting generators,it is important to understand what progress has already been made.Below we focus on the development history of ac synchronous generators,but parallel efforts for the ac synchronous motor,although not provided here,have also been considerable.Of course the basic design approach for motors is similar,excepting that motors convert electrical power into mechanical mo-tion whereas generators do the opposite.We will also not address the efforts in superconducting dc homopolar gener-ator/motor development (refer instead,for example,to [3,10]).3.1.Initial prototype LTSwork (late 1960s–1970s)One of the first US Air Force generator designs was an all-cryogenic,superconducting system that incorporated both a superconducting field winding and a superconduc-ting armature winding.This was a 50kW synchronous ma-chine designed by Dynatech in 1967[11].Although not successful,testing demonstrated the very real issue of ac losses in a superconducting armature ter machines used superconductors in the fieldwindingsFig.1.Cryogenic power system block diagram.P.N.Barnes et al./Cryogenics 45(2005)670–686673exclusively.In this case,a vacuum space must be used to separate the cryogenic field windings and room tempera-ture stator.Several small synchronous superconducting alternators with stationary superconducting field windings and con-ventional rotating armature windings were being con-structed by various groups.Examples of these occurred in the late 1960s and early 1970s throughout the world:an 8kVA machine in the United States (AVCO),a l00kVA machine in Russia,a 21kVA machine in Ger-many,and a 30kVA machine in Japan (Fuji Electric)[12].During the same time period,development of genera-tors with rotating field windings and stationary armature windings—more typical of later development efforts—were constructed and tested.Early efforts at MIT included a 45kVA device and later a 2MVA machine.A 1MVA machine was also built in the former Soviet Union.During this time,a two-pole,60Hz,5MVA machine with a rotating dewar assembly was built and tested by Westinghouse [13].Additionally,the US Air Force con-tracted Westinghouse to build a 5MVA,400Hz machine (Fig.3)[14].The 12,000rpm superconducting four-pole rotor designed for this machine was constructed and tested in 1974(without an armature),sustaining 240A at 12,000rpm—a speed appropriate for airborne applications and consistent with 5.32MVA operation.The alternator development program used NbTi in the rotor windings,necessitating 4.2K operation.Even so,the electromagnetic shield on the rotor was considered the most significant problem of the superconducting alternator,which caused excessive heating in the shield due to load-induced varying fields.This suggested that future designs have separate thermal and electromagnetic shields to avoid the heating problem [15].The combination of poor cooling and high losses placed strict design constraints on the superconduc-tor specifications.3.2.The second wave of LTS(late 1970s–1990s)The high rotational speeds achieved in the Westinghouse (US Air Force)program demonstrated that superconduc-ting field windings were capable of handling large centrifu-gal loads.This implied that much larger machine diameters were,in fact,feasible at the lower tip speeds used for 1000MVA commercial applications.In 1975,the Electric Power Research Institute (EPRI)contracted Westinghouse and General Electric to perform conceptual design studies for both a 300MVA and a 1200MVA superconducting generator for implementation by the power utility industry.This led to a follow-on program with Westinghouse on the 300MVA design,which ran until 1981[7].General Electric also built and tested a 20MVA superconducting generator in 1980using in-house funding.Working together,Mitsubishi Electric and Fuji Electric,under the support of the Ministry of International Trade and Industry (MITI)of the Japanese Government,con-structed and successfully tested a 6.25MVA,two pole,60Hz,3600rpm superconducting generator in 1977[16].This was the first machine with rotating superconducting field windings constructed in Japan.The field coils were wound with monolithic NbTi wire and consisted of nine separately impregnated coils for each pole.These compa-nies went on to develop another superconducting machine as a synchronous condenser with capacity of 30MVA in both leading and lagging phases,completed in 1982[16].Hitachi also constructed a superconducting generator with a 50MVA capacity.The rotor was completed in 1982and tested with a small stator [16].A 1000MVA generator was subsequently designed by Hitachi based on the 50MVA machine [17].International development (e.g.,in France,China,and Italy)of superconducting generators was also occurring in the late 1970s to early 1980s [18–20].At the Technical University of Munich in Germany,a 320kVA test genera-tor of the rotating-armature type was built to investigate the dynamic performance of superconducting generators.It was put in service in 1979and operated in the 1980s during the course of a long-range test program.Kraftwerk Union and Siemens of Germany also ran an extensive program to develop superconducting turbogenerators of commercial size for the electric utility industry [21].The Former Soviet Union tested a 20MVA turbogenerator in 1983[22].During the 1980s,General Electric built another 20MVA superconducting generator for the US Air Force (Fig.4).The field windings were made using Nb/Ti,with plans to retrofit with Nb 3Sn wire.During this time (1985),Massachusetts Institute of Technology built a 10MVA alternator [23].However,most LTS-based gener-ator efforts were curtailed with the discovery of HTS;re-search focused on the HTS conductor development due to the prospect of higher operating temperatures,especially liquid nitrogen operation.During the late 1980s,the MIT alternator program was probably the only significantUSFig.3.Superconducting NbTi-based 5MW generator,circa 1974,result-ing from an Air Force contract with Westinghouse.674P.N.Barnes et al./Cryogenics 45(2005)670–686dedicated effort other than the GE generator for the US Air Force for testing of ac synchronous superconducting machines which existed;the MIT effort continued into the early 1990s [24].Also during this timeframe,the US Air Force actively considered the use of high purity,composite,aluminum,cryogenic or ‘‘hyperconducting’’wire which,although not superconducting,had very low electrical resistance at $20K [25].As already mentioned,the combination of poor cooling and high losses in LTS windings imposed stringent design constraints on the superconductor.These concerns led to the development of a 40MW generator,incorporating high-purity aluminum in the windings.A 600kW exciter (shown in Fig.5)also using the high purity aluminum was constructed for the 40MW generator and weighed approximately 100kg [26].The copper stator windings were designed for operation at 20K as well.Based on the design and the data collected,it was estimated that the exciter could have provided 1MW of power,but the machine was not tested to this level.A main draw-back of the composite aluminum conductor was the use of liquid hydrogen,which has limited availability in most applications.Many concluded that HTS conductors should be more fully developed prior to continuing the superconducting generator work [25].This was not,however,the case in Japan where there were ongoing efforts in NbTi-based gen-erators throughout the 1990s.Successful tests in Japan and the United States of ac superconducting synchronous gen-erators convinced the Japanese government to launch a major national project on the application of superconduc-ting technologies to electric power apparatuses in mid 1987called the Engineering Research Association Project for Superconductive Generation Equipment and Materials (Super-GM).The first phase of Super-GM consisted of the design,construction,and test verification of three types of 70MW-class superconducting generators—two slow re-sponse and one quick response excitation types [27].The goal was to establish the technologies sufficiently to design and manufacture a 200MW-class pilot generator for com-mercial purposes.The Super-GM program was adminis-tered by the New Energy and Industrial Technology Development Organization (NEDO).For the Super-GM program,testing was completed in 1997on the first of the 70MW-class superconducting syn-chronous generators,slow response excitation type,with testing of the other two occurring in the next couple of years [28].The slow response excitation type rotors were built by Hitachi and Mitsubishi Electric.Toshiba built the quick response rotor.The LTS NbTi wire for these three rotors was supplied from three different Japanese companies.This program resulted in a record output of 79MW and the longest continuous operation at 1500hr [27].With the development of ultra-fine multifilamentary NbTi conductor,a more ac-tolerant superconducting wire,the prospect of making an all-cryogenic—or fully super-conducting—version of the ac synchronous machine was revitalized [29,30].In France,GEC ALSTHOM built and then tested an all-cryogenic 18kVA generator in 1990[31].As such,the thermal shielding was eliminated between rotor and stator and no electromagnetic shield was em-ployed.All the coils were monolayer and impregnated to minimize wire displacement.Because of the limited range of operating temperatures for LTS conductors,they can be quenched by frictional heating caused by abrupt motion of the wire.Testing of the generator included connection to an industrial power grid.Also in Japan,in 1994,testing of a superconducting armature winding made of NbTi was performed [32].This was for a 4pole,50Hz,30kVA class generator.Countermeasures were taken to minimize the ac loss degradation not only due to the electromagnetic fields the armature windings would experience,but also instabilities caused by conductor motion andvibration.Fig.4.General Electric 20MW LTS generator(1981).Fig.5.600kW cryogenic aluminum generator (exciter),1990.P.N.Barnes et al./Cryogenics 45(2005)670–686675The armature was wound with a cable consisting of22 strands specifically designed to minimize ac loss.Testing indicated that the incorporated countermeasures helped to reduce the losses due to acfields,but the rated armature current was not attained.Both of these efforts attest to the need for proper coil impregnation to prevent superconduc-tor motion.3.3.BSCCO based generators(mid-1990s-today)In the US,the Department of Energy(DOE)established the Superconductivity Partnership Initiative(SPI)Program to help fund the industrial development of HTS equipment in1993.Two of the funded programs initiated in1994in-cluded a125horsepower ac synchronous motor by Reli-ance Electric and an ac synchronous generator project led by General Electric.The generator program was directed at the conceptual design and assessment of a100MVA generator and the construction of a full-scale HTS race-track coil suitable for use in the generator.The coils,made of the HTS bismuth strontium calcium copper oxide (BSCCO),achieved the highfields necessary and in addi-tion,due to the higher20K operating temperature with greater heat capacity,the winding could tolerate a signifi-cantly higher transient heating[33].This implied that less electromagnetic shielding of thefield windings would be necessary.The testing provided great confidence in the use of HTS windings.AMSC and Westinghouse developed more up to date designs for HTS generators in the mid to latter1990s. One was a conceptual design for a50MW,3600-RPM HTS generator by AMSC[8].The other effort by Westing-house was sponsored by the Ballistic Missile Defense Office (BMDO)to provide high power for a mobile radar[34,35]. Westinghouse designed the power system so that the prime power unit would be a diesel engine for an1800rpm gen-erator capable of850kW at50V and150kW at120V. The rotor included four HTS coils for thefield winding and the stator had two sets of windings to supply simulta-neously both aforementioned voltages.A Gifford–McMa-hon refrigerator would provide the necessary cooling for the rotor by heat exchange.The overall effort included the incorporation of the newly developed BSCCO wire into the previously constructed600kW exciter for the 40MW aluminum design by retrofitting the composite alu-minumfield windings of the exciter with HTS BSCCOfield windings.The US Air Force initial funded American Superconductor in1992for the fabrication of four demon-stration BSCCO coils.In1996,BMDO funded fabrication of eight identical coils that were tested and met the required specification(72,000Amp-turn)for incorporation into the exciter.However,after the windings were delivered to Westinghouse to retrofit the exciter,two of the coils were destroyed during a welding process by a sub-contractor on the program.Additional funds were not available to correct this error andfinal testing of the generator never occurred.In2002,the University of Southampton in Great Britain has designed and started to build a simple100kVA high temperature superconducting(HTS)demonstrator genera-tor[36].This particular synchronous generator of the clas-sical superconducting type is a2-pole machine.The HTS rotor is designed to operate in the range of57–77K using either liquid nitrogen or air.To operate at these tempera-tures using BSCCO conductor,the normal component of the magneticfield will be directed away from the HTS con-ductor using magnetic invar rings between the adjacent HTS coils.To exclude ac magneticfields from the rotor, a cold copper screen will be placed around the rotor core.In2003,a1.5MVA high temperature superconducting generator has been very recently designed,built and suc-cessfully tested by the General Electric Company as an engineering prototype for a100MVA unit.The HTS coil in the1.5MVA demonstrator was designed to operate in the range of20–40K and is cooled with a closed cycle he-lium refrigeration system employing Gifford–McMahon cryocoolers.Predicted thermal losses were compared to those measured during rotor testing at3600rpm and found to be in close agreement.GE was just awarded a DOE-SPI contract for the design and development of the100MVA HTS generator[37].3.4.YBCO capable generators(starting2004)The US Air Force is also initiating new HTS generator development programs.As of2004,Long Electromagnetics (LEI)is currently constructing an HTS coil test rig or pseu-do generator.The test rig is designed for easier access to the field winding allowing the rotor coils to be replaced with alternate HTS coils for testing at high,>10,000rpm,rota-tional speeds.Initial coils of BSCCO will be used,but sub-sequently made YBCO coils can potentially be placed into the system.Simple stator windings are being included, hence a‘‘pseudo generator’’.It is expected to provide be-tween2–3MW power,but is an open cycle liquid hydrogen initial design(due to the BSCCO coils)as a result of budget constraints.An initial sketch of a more complete generator design is given in Fig.6.The US Air Force recently initi-ated a major HTS generator program,awarded to General Electric,in the latter part of2004for construction of a fully operational power system using BSCCO wire initially. Both of these systems will have the eventual potential to start the initial incorporation of the YBCO coated conduc-tor into the windings for military generators.Recently,Rockwell Automation of Ohio just demon-strated for thefirst time in2004a simple generator using only YBCO coils[38].The generator was built into a stan-dard5hp motor frame(Fig.7).It was a salient pole(iron core),four pole motor with four YBCOfield coils provided by SuperPower,Inc.consisting of20-turns of YBCO super-conducting tape,approximately5.9m in length and1.2cm in width,per coil.The generator had a liquid nitrogen cooled rotor via a shaft center transfer tube and slip rings for thefield current supply and for monitoring the coil volt-676P.N.Barnes et al./Cryogenics45(2005)670–686。

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High Power, High Efficiency, AlGaN/GaN HEMT Technology forWireless Base Station ApplicationsR.Vetury, Y.Wei, D.S.Green, S.R.Gibb, T.W.Mercier, K.Leverich, P.M.Garber, M.J.Poulton, J.B.Shealy RF Micro Devices, Infrastructure Product Line, Charlotte, NC, 28269, USAbstract — We report AlGaN/GaN high-electron-mobility-transistors (HEMT) on SiC substrates with field modulation plates (FP) of various dimensions and different gate widths. As a measure of the status of GaN technology achieved in this work, small periphery 150 µm HEMT demonstrated a continuous wave (CW) output power density of 22.7 W/mm at 2.14 GHz with power added efficiency (PAE) of 54% when biased at a drain-source voltage (V DS) of 80 V. As a demonstration of the scalability of this technology, a 20-mm-wide device exhibited 100 W CW output power and a simultaneous peak PAE of 55.3% at 2.14 GHz when biased at class AB and V DS=48V. WCDMA measurements on the 20mm part demonstrated ACP of –35 dBc at 42.5 dBm output power and 30% PAE under the same bias condition. Analysis of FP related performance tradeoffs are also presented in this work.Index Terms — Field plate, GaN, HEMT, WCDMAI. I NTRODUCTIONOver the past decade, AlGaN/GaN-based HEMT technology has emerged as a promising candidate for microwave power applications such as wireless base stations [1]. The competitive advantages of GaN HEMTs result from the material properties of the GaN/AlGaN material system and advantages afforded by various heterostructures possible in this material system [2-4]. Despite these material advantages over incumbent Si-LDMOS or GaAs technology, commercialization of GaN based HEMTs for wireless infrastructure applications has been hampered by the technological obstacles such as “current collapse” or “current slump” [3,5,6] and the high cost of SiC substrates. In this report, we present recent results and status of a manufacturable GaN technology developed at RFMD for wireless base station applications. AlGaN/GaN HEMT technology has made tremendous progress in the recent past, both in terms of maximum power density from small periphery devices [7] and total power output [8,9,10]. In AlGaN/GaN HEMT’s, the use of a field plate connected to the gate electrode has been shown to improve breakdown voltage and RF power performance [7,8]. Recently, 36 mm wide AlGaN/GaN HEMT based high power amplifiers (HPA’s) realized without FP’s were reported [9].However, there are few reports in the literature of a manufacturable GaN process technology achieving state-of-the-art power densities together with demonstrated scalability of the technology from small periphery “hero” devices to HPA’s, as characterized for base station applications. In this work, varied dimensions of field-plate are evaluated for understanding of tradeoffs between device performance metrics. We demonstrate AlGaN/GaN HEMTs on SiC developed for wireless infrastructure applications with state of the art device measurement results and high power amplifier WCDMA performance.II.D EVICE TECHNOLOGYFig 1 illustrates the AlGaN/GaN HEMT structure in our work. The AlGaN/GaN layer structure was grown by organometallic vapor phase epitaxy (OMVPE) on semi-insulating SiC. The GaN buffer layer was 2-µm thick. An undoped thin GaN cap layer was grown on the AlGaN barrier layer.There are generally two kinds of field plate structures reported. The so-called overlapping gate field plate structure [7] suffers from phase difference between gate and field plate because the field-plate is isolated from the gate over the device mesa. The phase difference between the two feed-in signals along the gate and field-plate cannot be neglected, especially for large periphery devices. The intimate contact of the gate and field plate in the structure of Fig. 1 eliminates this phase difference: a similar structure has been reported earlier by Ando [11]. Gate metal is formed from Ni/Au while a Ti/Al based metal scheme was used for source and drain ohmic contacts. On-wafer TLM demonstrated a contact resistivity of 0.18 Ω−mm. The devices were isolated by a mesa etch process.In this work, the gate length (L g ) and the gate to drain spacing (L gd ) was fixed at 0.6 um and 2.0 µm respectively . L fd is the field-plate dimension that was varied as 0.6, 1.0 and 1.4 µm.III. D EVICE PERFORMANCE AND ANALYSISA Cascade auto-probe station was used for on-wafer testing of all dc and small signal RF parameters using an Agilent 8720 Vector Network Analyzer and a 4145B semiconductor analyzer.a. Small signal RF Performance metricsThe maximum current-gain-cutoff frequency (f T ) and power-gain-cutoff frequency (f MAX ) were extracted using -20 dB/decade extrapolations from h 21 and Mason’s Gain respectively . A f T -f MAX map of 67 devices with gate width of 400 µm and field plate dimension, L fd of 0.6 µm on a 2” wafer is shown in Fig. 2. The devices were biased at V GS = -3.5 V and V DS = 10 V. As can be seen, Fig 2 shows excellent uniformity of f T and f MAX across the wafer.In order to understand the tradeoffs between frequency performance metrics with field plate dimension, the dependence of f T and f MAX on the FP dimension was investigated as a function of drain bias voltage for small periphery 2x200-µm wide devices. As shown in Fig 3, longer field-plate introduces larger C gd and results in lower f MAX and f T at all drain voltages. At higher drain bias voltage, the depletion layer under the field-plate extends toward the drain electrode: therefore f MAX increases with V DS due to the reduction of gate-drain capacitance (C gd ) and output conductance (G).Figure 2. f T -f MAX map of 67 devices, W g =0.4 mm, L fd =0.6 µm, V GS =-3.5 V and V DS =10 VDS fd L g =0.6 µm, W g =400 µm, biased at V GS =-3.5 V0.000.200.400.600.801.001.20246810121416V DS (V)I D C (A /m m ), I P _40 (A /m m )Figure 4 Pulsed IV plot of a 2x200 µm wide deviceb. Pulsed I-V performanceIn addition to dc and small signal RF measurements, pulsed IV test using an Accent DIVA 265 system were conducted, as shown in Fig. 4. A measure of the trapping effects that impact device performance can be obtained by examining the current recovery ratio (denoted CRR 540), which is defined as the ratio of dc current (I DC ) in the knee region (V DS =5V), to the pulsed current (I P-40) at the same V DS , but pulsed from a quiescent bias point of [Vds=40V and Vgs = -6V]. As can be seen from the inset in Fig. 4, this ratio is 0.89. While this ratio is relatively close to the ideal value of 1: it shows that there are transient and trapping effects to be overcome in this technology.c. Drain bias dependence of small periphery RF power performanceIn order to understand the capabilities of this technology, the large signal RF power performance of a small periphery (2x75µm) device was investigated over a range of drain bias : from 28V V DS to 80V V DS . RF power performance at 2.14 GHz was evaluated using a Maury loadpull system.The input and output match were tuned for the maximum output power at the 1-dB gain compression point. (P1-dB). Typically, devices could be biased up to 80Vand driven to (5-7) dB of compression, thus indicating that the breakdown voltage of this technology was more than adequate for 28V and 48V operation. Due to the soft rolloff exhibited by these GaN devices, saturated output power (P sat) was defined as the output power at the maximum PAE point, rather than at a fixed level of gain compression.satlinear gain, G T with V DS for a 2x75 µm device.Figure 6 Map of Psat and PAE of 150-µm wide devicesbiased at class-B and VDS=80 V.As can be seen from Fig 5, P sat increases linearly with V DS, while maximum PAE remained approximately constant (50-55%). This performance indicates that trapping effects that degrade PAE at higher drain biases [10], have been minimized to a large extent. The linear increase of P sat with V DS indicates that the maximum RF drain current stays constant over this range of drain bias, also indicating that trapping effects that cause RF current collapse have been minimized.To demonstrate across-wafer uniformity of this technology, large signal RF performance was measured on 14 2x75 µm devices distributed across a 2” wafer. The devices were biased at class B at a V DS of 80 V. As can be seen from the resulting wafer map of P sat and maximum PAE, shown in Fig 6, the maximum output power among this random selection of 14 devices is 22.7 W/mm with a corresponding maximum PAE of 54%.PAE (%) 0816243240-10-50510152025OutputPower(dBm),Gain(dB)Input Power (dBm)Fig. 7 Power performance of a 150-µm wide device with L fd of 1.0 µm.Fig. 7 shows a typical power performance of a 2x75 µm wide device with L fd of 1.0 µm. The input and output match were tuned for the maximum output power at the 1-dB gain compression point. (P1-dB). Output power density at the peak PAE point is 20.1 W/mm. The linear gain of the device was23.5 dB and the maximum PAE was 45.9 %.d. Large periphery GaN HPA PerformanceAs a demonstration of the scalability of this technology to large periphery HPA’s, devices with gate periphery of 20 mm were fabricated and tested at a Vds of 48V. Fig. 9 shows a die photograph of a 20-mm part. 20mm die were mounted in a flanged CuW package and pre-matched at 2.14 GHz for optimum gain and bandwidth. The HPA’s were biased into deep class AB (I ds=3 % I dmax). At V DS=48 V, 100 W output power was obtained with a simultaneous PAE of 55.3% (Fig. 10). The linear power gain was found to be 13.3 dB. At a drain voltage of 28V, the same part displayed 63 W P sat along with a peak PAE of 57.2%. T hese power performance metrics demonstrate the state of the art scalability of this technology to large periphery HPA’s.Figure 9 Die photograph of 20-mm HEMTFigure 10 Power performance of 20-mm HEMT biased at deep class-AB and V DS =48 V2.14 GHz WCDMA measurements employing TM1-16DPCH were conducted on a loadpull station . Biased in deep class AB, the PAE and ACPR of the 20-mm device versus output power at V DS =28 V and V DS =48 V are plotted in Fig. 11. At ACPR of –35 dBc and V DS of 28 V, the output power was 39 dBm and the PAE was 27.5%. At the same ACPR level when increased V DS to 48 V, 43-dBm output power was obtained with PAE of 30%. This indicates higher voltage operation at 48V should provide improved linearity Figure 11 WCDMA results of 20-mm HEMT biased at deep class-ABReliability analysis of this technology will be reported separately.IV. C ONCLUSIONIn summary, AlGaN/GaN HEMTs on SiC substrate with field-plate technology have been presented. 150-um wide HEMT demonstrated a continuous wave (CW) output power density of 22.7 W/mm at 2.14 GHz with power added efficiency (PAE) of 54% at V DS of 80 V . A 20-mm-wide device exhibited 100 W CW output power and a simultaneous PAE of 55.3% at 2.14 GHz when operated at deep class AB and V DS of 48V . Under the same testing condition, WCDMA measurement demonstrated ACPR of –35 dBc at 43-dBm output power and 30% PAE. These results demonstrate that AlGaN/GaN HEMTs can become a truly disruptive technology in the wireless base station arena.R EFERENCES[1] J. B. Shealy, , et al , “Gallium nitride (GaN) HEMT's: progress and potential for commercial applications ” Gallium Arsenide Integrated Circuit (GaAs IC) Symposium, 2002. 24th Annual Technical Digest , 20-23 Oct. 2002.[2] L. F. Eastman, et al, “The toughest transistor yet [GaN transistors],” Spectrum, IEEE , Vol: 39 , Issue: 5 , May 2002.[3] U.K. Mishra, et al , “AlGaN/GaN HEMTs-an overview of device operation and applications,” Proceedings of the IEEE , vol. 90, issue 6, pp.1022 – 1031, June 2002.[4] R.J. Trew, “SiC and GaN transistors - is there one winner for microwave power applications?” Proceedings of the IEEE , vol. 90, issue 6, pp.1032 – 1047, June 2002.[5] R. Vetury, et al , “The impact of surface states on the DC and RF characteristics of AlGaN/GaN HFETs,” Transactions on Electron Devices, Volume: 48 , Issue: 3, pp. March 2001.[6] L. F. Eastman, et al, “Undoped AlGaN/GaN HEMTs for microwave power amplification,” Electron Devices, IEEE Transactions on, Volume: 48 , Issue: 3 , March 2001.[7] Y.-F. Wu, et al , “30-W/mm GaN HEMTs by field plate optimization.,” IEEE Electron Device Letters , vol. 25, issue 3, pp.117-119, March 2004.[8] Y. Okamoto, “179 W recessed-gate AlGaN/GaN heterojunction FET with field-modulating plate,” IEEE Electronics Letters , vol. 40, issue: 10 , pp. 629 – 631, May 2004.[9] T. Kikkawa, et al , “An over 200-W output power GaN HEMT push-pull amplifier with high reliability,” Microwave Symposium Digest, 2004 IEEE MTT-S International , vol. 3, pp.1347–1350, June 2004.[10] P. Parikh , , et al , “AlGaN-GaN HEMTs: material, device, circuit technology and applications,” Compound Semiconductors, 2003. International Symposium , 25-27 Aug. 2003.[11] Y. Ando, et al , ”10-W/mm AlGaN-GaN HFET with a field modulating plate,” IEEE Electron Device Letters , vol. 24 , issue 5, pp.289–291, May 2003.。

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