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COUDREUSE: ‘A new approach to low cycle fatigue behaviour of a duplex stainless steel based on the deformation mechanisms of the individual phases’, STP 942, 812; 1988, Philadelphia, PA, ASTM.",{"doi":524},"10.1520\u002FSTP24523S",{"id":24,"text":526,"url":24,"identifiers":527},"M. JACOBSSON: ‘Fatigue testing of the duplex grades SAF 2304, SAF 2205 and SAF 2507’, Internal Report no. 6060, Sandvik Steel, Sandviken, Sweden, 1991.",{},{"id":24,"text":529,"url":24,"identifiers":530},"J. MOSKOVITZ and R. PELLOUX: ‘Corrosion fatigue technology’, STP 642, 133; 1978, Philadelphia, PA, ASTM.",{"doi":531},"10.1520\u002FSTP28718S",{"id":24,"text":533,"url":24,"identifiers":534},"10.1007\u002FBF02648710",{"doi":533},{"id":24,"text":536,"url":24,"identifiers":537},"A. G. HAYNES: ‘Duplex and high alloy corrosion resisting steels’ Lloyd's Register Technical Association paper no. 6. 1990-1991, p. 1.",{},{"id":24,"text":539,"url":24,"identifiers":540},"10.1016\u002F0956-7151(91)90224-O",{"doi":539},{"id":24,"text":542,"url":24,"identifiers":543},"LORENTZ K., 1969, Thyssen Forschung, 1, 97",{},{"id":24,"text":545,"url":24,"identifiers":546},"10.1002\u002Fmaco.19840351202",{"doi":545},{"id":24,"text":548,"url":24,"identifiers":549},"10.5006\u002F0010-9312-35.4.151",{"doi":548},{"id":24,"text":551,"url":24,"identifiers":552},"10.5006\u002F1.3577327",{"doi":551},{"id":24,"text":554,"url":24,"identifiers":555},"10.1149\u002F1.2129046",{"doi":554},{"id":24,"text":557,"url":24,"identifiers":558},"10.5006\u002F1.3593843",{"doi":557},{"id":24,"text":560,"url":24,"identifiers":561},"HONGLU C., ‘Kinetics of intermetallic phase formation in duplex stainless steels and their influence on corrosion resistance’, 1991",{},{"id":24,"text":563,"url":24,"identifiers":564},"10.5006\u002F1.3582052",{"doi":563},{"id":24,"text":566,"url":24,"identifiers":567},"S. 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GILBERT: ‘Duplex stainless steels’, 83; 1986, The Hague, The Netherlands, Nederlands Instituut voor Lastechniek.",{},{"id":24,"text":605,"url":24,"identifiers":606},"10.1007\u002FBF02811664",{"doi":605},{"id":24,"text":608,"url":24,"identifiers":609},"PAK s., 1992, ‘Welding the super duplex stainless steel Zeron 100’, Elektro svets a",{},{"id":24,"text":611,"url":24,"identifiers":612},"A. CIGADA, S. DeMARTIIS, G. RONDELLI, B. VINCENTINI, M. GIACOMAZZI, and A. RODS: ‘Stainless steels '91’, Chiba, Japan, 10-13 June 1991, The Iron and Steel Institute of Japan, p. 716.",{},{"id":614,"createTime":615,"updateTime":615,"relativeEntities":616,"slug":617,"properties":618,"entityType":147,"verifyStatus":630,"verifyTime":615,"verifyNote":631,"syncStatus":23,"languages":632,"translateLanguages":24,"viewCount":25,"primaryUrl":633,"fullTextUrl":24,"authors":634,"publicationType":223,"publisherRelationship":670,"citationCount":703,"citationInfo":704,"publishDate":706,"publishYear":707,"citationAnalyzeStatus":23,"lastCitationAnalyze":24,"indexDatabases":24,"openAccess":24,"references":708,"isForceReanalyzing":325},"e4200b17-df97-4248-bd39-70c5ce300d60","2024-09-01T23:24:05.452+00:00",[],"Visual-analysis-of-solidification-and-i-%CE%B4-i-i-%CE%B3-i-transformations-in-steels",{"mag":619,"keywords":621,"openalex":622,"abstract":624,"title":626,"doi":628},{"VOID":620},"2019857891",{},{"VOID":623},"W2019857891",{"EN":625},"\u003Cjats:p> The theory of solidification of steels and the kinetics of austenite to α-ferrite phase transformation were extensively studied; however, comparatively, little information is available concerning the kinetics of the δ-ferrite to austenite transformation due to the difficulty of making in situ observations. In the present study, a laser scanning confocal microscopy with an infrared image furnace was implemented with which the in situ observations at the high temperature of the dynamic behaviour of the δ\u002F γ grain nucleation and growth and interphase boundaries of the steels are made possible. The solidification mode of the carbon steel and the austenitic stainless steel during welding can be directly observed, and the definitive sequence of phase transformation that led to the final microstructure was detected in real time. Finally, new experimental results will be presented and compared with previous studies. \u003C\u002Fjats:p>",{"EN":627},"Visual analysis of solidification and \u003Ci>δ\u003C\u002Fi>–\u003Ci>γ\u003C\u002Fi> transformations in steels",{"VOID":629},"10.1179\u002F1743284712y.0000000183","VERIFIED","Auto 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The PWHT was carried out at aging temperature of 165°C for 18 h. The mechanical properties of the joints were evaluated using tensile tests. The experimental results indicate that the PWHT significantly influences the tensile properties of the FSW joints. After the heat treatment, the tensile strength of the joints increases and the elongation at fracture of the joints decreases. The maximum tensile strength of the joints is equivalent to 89% of that of the base material. The fracture location characteristics of the heat treated joints are similar to those of the as welded joints. The defect free joints fracture in the heat affected zone on the retreating side and the joints with a void defect fracture in the weld zone on the advancing side. 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1",{},{"id":24,"text":1331,"url":24,"identifiers":1332},"10.4028\u002Fwww.scientific.net\u002FDDF.283-286.65",{"doi":1331},{"id":24,"text":1334,"url":24,"identifiers":1335},"10.1016\u002Fj.msea.2018.05.033",{"doi":1334},{"id":24,"text":1337,"url":24,"identifiers":1338},"10.1115\u002F1.3226059",{"doi":1337},{"id":24,"text":1340,"url":24,"identifiers":1341},"10.1016\u002Fj.jmatprotec.2018.09.034",{"doi":1340},{"id":24,"text":1343,"url":24,"identifiers":1344},"10.1016\u002Fj.matpr.2018.10.324",{"doi":1343},{"id":24,"text":1346,"url":24,"identifiers":1347},"10.1016\u002Fj.msea.2019.138698",{"doi":1346},{"id":24,"text":1349,"url":24,"identifiers":1350},"10.1016\u002Fj.msea.2018.07.012",{"doi":1349},{"id":24,"text":1352,"url":24,"identifiers":1353},"10.1016\u002Fj.actamat.2012.11.045",{"doi":1352},{"id":1355,"createTime":1356,"updateTime":1356,"relativeEntities":1357,"slug":1358,"properties":1359,"entityType":147,"verifyStatus":23,"verifyTime":1371,"verifyNote":148,"syncStatus":23,"languages":1372,"translateLanguages":24,"viewCount":25,"primaryUrl":1373,"fullTextUrl":24,"authors":1374,"publicationType":223,"publisherRelationship":1386,"citationCount":1419,"citationInfo":1420,"publishDate":1424,"publishYear":1425,"citationAnalyzeStatus":23,"lastCitationAnalyze":24,"indexDatabases":24,"openAccess":24,"references":1426,"isForceReanalyzing":325},"da0e1d26-4ba3-400c-b9a4-129e11c18880","2024-09-19T22:43:24.403+00:00",[],"Gas-tungsten-arc-welding-of-i-%CE%B1-i-i-%CE%B2-i-titanium-alloys-A-review",{"mag":1360,"keywords":1362,"openalex":1363,"abstract":1365,"title":1367,"doi":1369},{"VOID":1361},"2022121818",{},{"VOID":1364},"W2022121818",{"EN":1366},"\u003Cjats:p> Titanium alloys used in aerospace structures require joints of high integrity to meet the design requirements. Gas tungsten arc welding (GTAW), laser beam welding (LBW) and electron beam welding (EBW) are all processes capable of creating fusion welded joints. Gas tungsten arc welding offers the potential to achieve welds of equal quality to EBW or LBW at much lower capital costs; however, the application of GTAW involves gaining an understanding of the complex process characteristics. This paper reviews the process characteristics for GTAW titanium alloys and compares these characteristics with EBW and LBW titanium alloys. The characteristics of active flux tungsten inert gas welding and keyhole mode GTAW, two recent developments to GTAW, are considered, as is keyhole mode plasma arc welding. These variants are capable of greater penetration and, in some cases, faster processing speeds than conventional GTAW. Finally, the current knowledge of weld microstructural development in cast and wrought α + β titanium alloys and the mechanical performance of such welded joints are examined. Notably, conduction mode GTAWs are shown to have comparable mechanical properties with EBWs in relation to both cast and wrought base metals. \u003C\u002Fjats:p>",{"EN":1368},"Gas tungsten arc welding of \u003Ci>α\u003C\u002Fi> + \u003Ci>β\u003C\u002Fi> titanium alloys: A review",{"VOID":1370},"10.1179\u002F174328408x389463","2024-09-19T22:43:24.402+00:00",[150],"https:\u002F\u002Fjournals.sagepub.com\u002Fdoi\u002Ffull\u002F10.1179\u002F174328408X389463",[1375],{"id":1376,"sortIndex":25,"researcher":24,"roles":1377,"affiliations":1378,"properties":1379},"56a0e52f-3868-4fad-8f07-ea4cec987438",[],[],{"openalex":1380,"orcid":1382,"title":1384},{"VOID":1381},"A5069605571",{"VOID":1383},"https:\u002F\u002Forcid.org\u002F0000-0001-6546-3004",{"EN":1385},"Andrew Short",{"url":24,"publisher":1387,"properties":1412},{"id":6,"createTime":7,"updateTime":8,"relativeEntities":1388,"slug":10,"properties":1389,"entityType":22,"verifyStatus":23,"verifyTime":24,"verifyNote":24,"syncStatus":23,"languages":24,"translateLanguages":24,"viewCount":25,"subjectFields":1395,"manageAffiliations":1396,"indexDatabases":1397,"url":126,"thumbnailPath":24,"statistic":24,"gsStatistic":24,"type":24,"analyzePriority":24},[],{"country":1390,"issn":1391,"introduce":1392,"eissn":1393,"title":1394},{"VOID":13},{"VOID":15},{"EN":17},{"VOID":19},{"EN":21},[],[],[1398,1405],{"id":105,"indexDatabase":1399,"url":118,"indexYears":119,"academicFieldIds":1404,"indexDatabaseRanking":125},{"id":107,"createTime":108,"updateTime":109,"relativeEntities":1400,"label":1401,"description":1402,"key":115,"publicationTags":1403,"standard":24},[],{"EN":112,"VI":112},{"EN":112,"VI":114},[117],[121,122,123,124],{"id":85,"indexDatabase":1406,"url":100,"indexYears":24,"academicFieldIds":1411,"indexDatabaseRanking":24},{"id":87,"createTime":88,"updateTime":89,"relativeEntities":1407,"label":1408,"description":1409,"key":96,"publicationTags":1410,"standard":24},[],{"EN":92,"VI":92},{"VI":94,"EN":95},[98,99],[102,103],{"volume":1413,"pages":1415,"issue":1417},{"VOID":1414},"25",{"VOID":1416},"309-324",{"VOID":1418},"3",110,{"total":1419,"publishYear":24,"statisticByYear":1421},{"2012":807,"2013":806,"2014":260,"2015":176,"2016":155,"2017":807,"2018":703,"2019":808,"2020":806,"2021":1422,"2022":1423,"2023":808,"2024":1423},14,11,"2009-03-01",2009,[1427,1430,1433,1436,1439,1442,1445,1448,1451,1454,1457,1460,1463,1466,1469,1473,1476,1479,1482,1485,1488,1491,1494,1497,1501,1504,1507,1510,1513,1516,1519,1522,1525,1528,1531,1534,1537,1540,1543,1546,1549,1552,1555,1558,1561,1564,1567,1570,1573,1576,1579,1583,1586,1589,1592,1595,1598,1601,1604,1607,1610,1613,1616,1619,1622,1626,1629,1632,1635,1638,1641,1644,1647,1650,1653,1656,1659,1662,1665,1668,1671,1674,1677,1680,1683,1686,1689,1692,1695,1698,1701,1704,1707,1710,1713,1716,1719,1722,1725,1728,1731,1734,1737,1740],{"id":24,"text":1428,"url":24,"identifiers":1429},"Baeslack W. 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Processes, 159, 39",{},{"id":24,"text":1467,"url":24,"identifiers":1468},"Hilton P., Blackburn J.,  and Chong P.: ICALEO 2007, Orlando, FL, USA, 29 October-1 November 2007, Laser Institute of America,887–895.",{},{"id":24,"text":1470,"url":24,"identifiers":1471},"Tanaka M., 2007, J. Phys. D: AppL Phys, 40, 10.1088\u002F0022-3727\u002F40\u002F5\u002F027",{"doi":1472},"10.1088\u002F0022-3727\u002F40\u002F5\u002F027",{"id":24,"text":1474,"url":24,"identifiers":1475},"10.1179\u002F174329305X57509",{"doi":1474},{"id":24,"text":1477,"url":24,"identifiers":1478},"10.1179\u002F136217100101538191",{"doi":1477},{"id":24,"text":1480,"url":24,"identifiers":1481},"Lucas W. ‘TIG and plasma welding: process techniques, recommended practices and applications': 1990, Abington, Cambridge, UK, Woodhead Publishing.",{},{"id":24,"text":1483,"url":24,"identifiers":1484},"10.1179\u002F136217100322910624",{"doi":1483},{"id":24,"text":1486,"url":24,"identifiers":1487},"Marya S.: IIW Doc. 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Conf. on ‘Trends in welding research’, Callaway Gardens Resort, Pine Mountain, GA, USA, 16-20 May 2005, ASM International, 577",{},{"id":24,"text":1562,"url":24,"identifiers":1563},"Smith L., Gittos M.,  and Threadgill P. ‘High quality and productivity joining processes and procedures for titanium risers and flowlines’, Trondheim, Norway, 1999, SINTEF.",{},{"id":24,"text":1565,"url":24,"identifiers":1566},"Grong O. ‘Metallurgical modelling of welding’: 1994, London, The Institute of Materials.",{},{"id":24,"text":1568,"url":24,"identifiers":1569},"Easterling K. E. ‘Introduction to the physical metallurgy of welding’: 1992, Oxford, UK, Butterworth-Heinemann Ltd.",{},{"id":24,"text":1571,"url":24,"identifiers":1572},"L&üfiering G.,  and Williams J. C. ‘Titanium’, 379; 2003, Berlin, Springer.",{},{"id":24,"text":1574,"url":24,"identifiers":1575},"Peters J. O., MetalL Mater. Trans. A, 2001, 32A, 2805",{},{"id":24,"text":1577,"url":24,"identifiers":1578},"Harwig D. D., Fountain C., Ittiwattana W.,  and Castner H.: Weld 1, 2000, 79, 305s-316s.",{},{"id":24,"text":1580,"url":24,"identifiers":1581},"Mishra S.,  and DebRoy T.: Acta Mater. 2004, 52, 1183–1192.",{"doi":1582},"10.1016\u002Fj.actamat.2003.11.003",{"id":24,"text":1584,"url":24,"identifiers":1585},"10.1179\u002Fimr.1975.20.1.83",{"doi":1584},{"id":24,"text":1587,"url":24,"identifiers":1588},"10.1007\u002Fs11661-999-1011-y",{"doi":1587},{"id":24,"text":1590,"url":24,"identifiers":1591},"10.1081\u002FAMP-200041857",{"doi":1590},{"id":24,"text":1593,"url":24,"identifiers":1594},"Jones S. A., 2003, ‘Refinement of Ti6A14V weld metal structures during gas-tungsten arc welding’",{},{"id":24,"text":1596,"url":24,"identifiers":1597},"10.1179\u002F174328006X102493",{"doi":1596},{"id":24,"text":1599,"url":24,"identifiers":1600},"10.1557\u002FJMR.2008.0002",{"doi":1599},{"id":24,"text":1602,"url":24,"identifiers":1603},"10.1016\u002Fj.scriptamat.2005.08.020",{"doi":1602},{"id":24,"text":1605,"url":24,"identifiers":1606},"Neuberger B. W., 2004, ‘Dynamics of near-alpha titanium welding’",{},{"id":24,"text":1608,"url":24,"identifiers":1609},"10.1179\u002F174329306X120750",{"doi":1608},{"id":24,"text":1611,"url":24,"identifiers":1612},"10.1007\u002FBF00579271",{"doi":1611},{"id":24,"text":1614,"url":24,"identifiers":1615},"10.1016\u002FS0921-5093(98)01010-7",{"doi":1614},{"id":24,"text":1617,"url":24,"identifiers":1618},"10.1179\u002F136217199101537699",{"doi":1617},{"id":24,"text":1620,"url":24,"identifiers":1621},"10.1179\u002F174329306X77083",{"doi":1620},{"id":24,"text":1623,"url":24,"identifiers":1624},"Yang Z., Sista S., Elmer J. W.,  and Debroy T.: Acta Mater. 2000, 48, 4813–4825.",{"doi":1625},"10.1016\u002FS1359-6454(00)00279-2",{"id":24,"text":1627,"url":24,"identifiers":1628},"10.1016\u002FS0921-5093(97)00802-2",{"doi":1627},{"id":24,"text":1630,"url":24,"identifiers":1631},"Gould J. E., Proc. 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A, 1998, A243,32–45.",{},{"id":24,"text":1693,"url":24,"identifiers":1694},"10.1007\u002Fs11661-006-0028-8",{"doi":1693},{"id":24,"text":1696,"url":24,"identifiers":1697},"10.1088\u002F0957-0233\u002F15\u002F1\u002F001",{"doi":1696},{"id":24,"text":1699,"url":24,"identifiers":1700},"Tiley J., 2002, ‘Modeling of microstructure property relationships in Ti-6A1-4V’",{},{"id":24,"text":1702,"url":24,"identifiers":1703},"10.1016\u002Fj.msea.2003.12.008",{"doi":1702},{"id":24,"text":1705,"url":24,"identifiers":1706},"10.1361\u002F10599490418424",{"doi":1705},{"id":24,"text":1708,"url":24,"identifiers":1709},"Wei Y. H., 2005, J. Mater. Sci. 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The reinforcing phase was a Zr\u003Cjats:sub>57\u003C\u002Fjats:sub>Cu\u003Cjats:sub>20\u003C\u002Fjats:sub>Al\u003Cjats:sub>10\u003C\u002Fjats:sub>Ti\u003Cjats:sub>8\u003C\u002Fjats:sub>Ni\u003Cjats:sub>5\u003C\u002Fjats:sub> metallic glass (MG) and the matrix phase consisted of two types of aluminium powders with similar particle sizes but different strengths (pure aluminium and 5083 alloy). Damage mechanisms in tension were characterised quantitatively by X-ray tomography using in situ tensile tests. The transition in the initiation of damage between matrix shearing, inclusion fracture or matrix-inclusion debonding is presented and discussed as a function of the material's microstructure. \u003C\u002Fjats:p>",{"EN":1755},"Damage characterisation in aluminium matrix composites reinforced with amorphous metal inclusions",{"VOID":1757},"10.1179\u002F1743284714y.0000000619","2024-09-25T22:37:23.987+00:00",[150],"https:\u002F\u002Fjournals.sagepub.com\u002Fdoi\u002Ffull\u002F10.1179\u002F1743284714Y.0000000619",[1762,1784,1799],{"id":1763,"sortIndex":81,"researcher":24,"roles":1764,"affiliations":1765,"properties":1777},"c0934d19-dc44-4a52-b9a7-7d5e27af769b",[],[1766],{"id":1767,"sortIndex":25,"affiliation":1768,"properties":24},"6b145f43-3e08-4ca9-8036-194889db45ef",{"id":1769,"createTime":1770,"updateTime":1771,"relativeEntities":1772,"slug":1773,"properties":1774,"entityType":69,"verifyStatus":23,"verifyTime":24,"verifyNote":24,"syncStatus":23,"languages":24,"translateLanguages":24,"viewCount":25},"7b4a5c15-cc31-4b8b-9270-d805eb0824cc","2024-02-06T17:55:55.882+00:00","2024-10-13T05:50:19.910+00:00",[],"MATEIS-INSA-Lyon-CNRS-UMR5510-F-69621-France",{"title":1775},{"VI":1776},"MATEIS, INSA-Lyon, CNRS UMR5510, F-69621, France",{"openalex":1778,"orcid":1780,"title":1782},{"VOID":1779},"A5038738752",{"VOID":1781},"https:\u002F\u002Forcid.org\u002F0000-0003-1952-2602",{"EN":1783},"Éric Maire",{"id":1785,"sortIndex":25,"researcher":24,"roles":1786,"affiliations":1787,"properties":1794},"c024ee24-9af0-41db-baa1-e762b0b7f5ec",[],[1788],{"id":1789,"sortIndex":25,"affiliation":1790,"properties":24},"386256da-b126-423e-b907-1c4eba01dbfa",{"id":1769,"createTime":1770,"updateTime":1771,"relativeEntities":1791,"slug":1773,"properties":1792,"entityType":69,"verifyStatus":23,"verifyTime":24,"verifyNote":24,"syncStatus":23,"languages":24,"translateLanguages":24,"viewCount":25},[],{"title":1793},{"VI":1776},{"openalex":1795,"title":1797},{"VOID":1796},"A5005656598",{"EN":1798},"A. 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As-cast alloys with different silicon contents and an ex-service tube are submitted to laboratory agings to trigger specific phase transformations, and subsequently creep-tested at 950°C under stresses of 24–48 MPa. As-cast microstructures contain interdendritic chromium-rich M\u003Cjats:sub>7\u003C\u002Fjats:sub>C\u003Cjats:sub>3\u003C\u002Fjats:sub> carbides with niobium-rich MC carbides. After aging at 950°C, primary M\u003Cjats:sub>7\u003C\u002Fjats:sub>C\u003Cjats:sub>3\u003C\u002Fjats:sub> carbides transform into chromium-rich M\u003Cjats:sub>23\u003C\u002Fjats:sub>C\u003Cjats:sub>6\u003C\u002Fjats:sub> carbides, associated to a loss in creep strength. The G phase present in the ex-service alloy is reversed into MC carbides by a heat treatment at 1100°C, associated to a slight decrease in creep resistance. Besides, the addition of silicon is highly detrimental to creep strength. Results can be used for alloy design. \u003C\u002Fjats:p>",{"EN":1991},"Creep resistance of Fe–Ni–Cr heat resistant alloys for reformer tube applications",{"VOID":1993},"10.1080\u002F02670836.2019.1648371",[150],"https:\u002F\u002Fjournals.sagepub.com\u002Fdoi\u002Ffull\u002F10.1080\u002F02670836.2019.1648371",[1997,2016,2038],{"id":1998,"sortIndex":155,"researcher":24,"roles":1999,"affiliations":2000,"properties":2011},"9b76062e-33f6-4356-823c-8f7909314f9d",[],[2001],{"id":2002,"sortIndex":25,"affiliation":2003,"properties":24},"1f3459b3-1d15-4ee4-9545-5f9795d57058",{"id":2004,"createTime":2005,"updateTime":2005,"relativeEntities":2006,"slug":2007,"properties":2008,"entityType":69,"verifyStatus":23,"verifyTime":24,"verifyNote":24,"syncStatus":23,"languages":24,"translateLanguages":24,"viewCount":25},"68c01be9-07c7-4dd0-8d7f-45bfdac4d9f6","2024-09-03T22:24:31.778+00:00",[],"Air-Liquide-Si%C3%A8ge-Social-",{"title":2009},{"EN":2010},"Air Liquide [Siège 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The properties of cast 25 per cent chromium-20 per cent nickel austenitic steels in relation to their use at elevated temperatures. 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