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Weldability of Invar and Its Large-Diameter Pipe

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Weldability of Invar and Its Large-Diameter Pipe Weldability of Invar and Its Large-Diameter Pipe Hot-cracking resistance of reheated Invar weld metal is improved by reducing sulfur and impaired by adding titanium and boron BY T. OGAWA ABSTRACT. Sulfur remarkably increases Based on these results, a 60-ton heat fact, several papers have reported that the hot-cracking susceptibility of the was made in a mill run, and it was the weld bead reheated on multi-pass reheated Invar weld metal in the double- wrought and cold-rolled to 0.5-, 0.7- and welding or repair welding has a high bead Varestraint test. The detrimental 1.5-mm (0.02-, 0.03- and 0.06-in.)-gauge tendency to crack (Refs. 4, 15, 16). Partic­ effect of sulfur is so great that its content sheets. These sheets were welded in ularly, the earlier extensive research should be reduced to less than 0.002% in butt, fillet and edge joints, all of which report by C. E. Witherell (Ref. 13) has order to attain the high cracking resis­ resulted in satisfactory weldment proper­ been quite suggestive, and pointed out a tance as compared to Type 300 series ties. From another mill heat, the 11.0-mm conspicuously preferential effect of an stainless steels. The morphology of (0.4-in.)-thick, 66-cm (26-in.)-diameter addition of titanium and manganese to impact fracture surfaces of the reheated and 5-m (16.4-ft)-long welded pipes were improve the hot-cracking susceptibility of weld metal at -196°C (-321 °F) is closely made in a production run using the Invar. On the other hand, in the mill related to the sulfur content. The GTAW and plasma arc welding process­ process of making high nickel-iron alloys materials, the sulfur content of which is es. No cracks or discontinuities could be such as Invar, some troublesome prob­ decreased to less than 0.002%, result in found in seam and girth welds, and the lems have been experienced, namely, a completely ductile fracture, while the fracture surfaces of tested material at greatly accelerated oxidation of the slab ones bearing more than 0.002% sulfur -196CC were completely ductile with ingot surfaces in the heating furnace, clearly exhibit a typical habit of columnar superb toughness. leading to heavy cracks in the hot-rolling grain boundary with brittle-like fracture process, which seem to be involved in surfaces. the common cracking mechanism on Introduction multi-run welds. Therefore, more than 50 Cracking in the reheated Invar weld experimental heats were made to exten­ metal occurs in two ways, each working Invar, 36% Ni-Fe steel (Refs. 1-3), has a sively investigate and clarify the effects of independently or reciprocally. One is the very small thermal expansion coefficient, the chemical compositions on hot-crack­ liquation of some low-melting constitu­ good formability, and excellent tough­ ing susceptibility on welding in order to ents in the grain boundary of the weld ness, especially at low temperature. This expand the range of Invar's application to metal, caused by the reheating of the is due to its austenitic structure. There large welded steel structures. Based on weld metal by a subsequent pass. Anoth­ have long been active moves toward the these results, 11.0-mm-thick Invar plates er is the grain boundary embrittlement use of Invar for cryogenic service storage have been developed and, on a produc­ caused by the formation and growth of vessels, utilizing its small thermal expan­ tion basis, the 66-cm-diameter, 5-m-long various compounds on the succeeding sion coefficient feature. Examples are large welded pipe of this alloy was made weld runs. seen in its use for LNG carriers in France and Sweden, and for liquid fuel transport for LNG applications. Evaluation was Some titanium and boron additions to made of the various performance prop­ Invar increased markedly the hot-crack­ pipe by NASA (Refs. 4-6). Technological developments are being pursued in the erties and the reliability and integrity of ing susceptibility of the reheated weld welded joints of Invar to determine its metal by the subsequent pass. Chromi­ application of Invar for large under­ ground LNG membrane tanks, as demon­ useability in large welded steel struc­ um, which essentially gives rise to an tures. increase of the intrinsic thermal expan­ strated in the Gas Transport-McDonnell sion coefficient of Invar, has a beneficial Douglas method (Refs. 7, 8). effect for suppressing the crack occur­ Compared with Type 304 austenitic Experimental Procedure rence in the reheated weld metals. stainless steel, which is widely used for corrosion-resistant storage vessels, Invar The chemical compositions of the is rather expensive and somewhat differ­ experimental Invar heats studied are Paper presented at the 66th Annual AWS ent in weldability and corrosion resis­ listed in Tables 1 and 2. Those of the two Meeting, held April 29 to May 3, 1985, in Las tance. For these reasons, Invar was used 60-ton heats made on a mill production Vegas, Nev. mostly in 0.5- to 2.0-mm (0.02- to 0.08- basis, commercially available Invar sheet, in.)-thick gauge sheet. T. OCAWA is a Senior Researcher, Welding and austenitic stainless steels commonly Technology Lab, R&D Laboratories 11, Nippon Since Invar is a fully austenitic steel, it used are also listed in Table 2. Experimen­ Steel Corp., Fuchinobe Sagamihara Kanagawa, has been presumed that hot cracking is tal 25- and 50-kg (11- and 22-lb) ingots lapan. likely to occur on welding (Refs. 9-14). In were forged, rolled, and finally solution WELDING RESEARCH SUPPLEMENT | 213-s Table 1—Chemical Compositions of Laboratory Heats (25 kg) Heat Ni Mn O Al Cr Note D 35.23 0.003 0.02 <0.01 0.0009 0.0003 0.0053 - 0.17 0.0006 low c, Si, Mn Q 35.82 0.018 0.15 0.20 0.0007 0.0003 0.0027 - 0.17 0.0005 <* 1 K 35.62 0.016 0.14 0.23 0.0004 0.003 0.0030 0.17 0.0010 od — CO R 35.82 0.018 0.15 0.20 0.0007 0.005 0.0024 - 0.17 0.0006 co O 35.49 0.018 0.16 0.21 0.0002 0.014 0.0017 0.17 0.0005 - (N L 35.5 0.020 0.15 0.20 0.0008 0.0006 - - 0.14 — M 35.5 0.020 0.15 0.20 0.0070 <0.001 - - 0.14 - DC E 35.6 0.017 0.15 0.21 0.0120 0.0003 0.0030 - 0.13 - CU u_ F 35.6 0.017 0.15 0.21 0.0160 0.0003 0.0015 - 0.13 0.0005 0) G 35.5 0.020 0.15 0.20 0.0040 0.005 - - 0.14 0.0005 % I J 911 34.1 0.002 0.07 0.01 0.003 0.002 0.044 0.002 0.01 0.0015 ,. 912 35.2 0.001 0.01 0.01 0.003 0.002 0.045 0.002 0.01 0.0013 913 36.5 0.001 0. () I 0.01 0.003 0.003 0.043 0.002 0.01 0.0012 z 921 35.6 0.014 0.15 0.30 0.003 0.0016 0.0024 0.007 0.18 0.0017 c, 922 35.5 0.027 0.15 0.30 0.003 0.0018 0.0025 0.007 0.18 0.0012 U u 35.4 0.003 923 0.049 0.15 0.30 0.00 16 0.0025 0.006 0.18 0.0015 0) 931 35.3 0.022 0.09 0.33 0.003 0.0016 0.0015 0.016 0.15 0.0014 ,|J3 *Z 932 35.4 0.020 0.18 0.33 0.003 0.0016 0.0015 0.016 0.16 0.0012 O lo Ol 3 933 35.3 0.018 0.27 0.33 0.003 0.00 16 0.0013 0.016 0.17 0.0013 c u1 .Q 941 35.8 0.023 0.10 0.10 0.002 0.0018 0.0117 0.003 0.13 0.0018 c 942 35.6 0.019 0.10 0.33 0.002 0.0019 0.0087 0.002 0.14 0.0017 5 DO 943 35.8 0.015 0.10 0.44 0.002 0.0017 0.0083 0.002 0.16 0.0017 u 03 951 35.8 0.021 0.15 0.31 0.002 0.0023 0.0055 0.002 0.13 0.0013 a J > 952 35.9 0.022 0.15 0.31 0.002 0.0019 0.0067 0.002 0.30 0.0014 ( ) co 953 35.6 0.019 0.15 0.31 0.002 0.0021 0.0058 0.002 0.51 0.0015 971 35.8 0.020 0.16 0.30 0.002 0.0022 0.0065 0.001 0.15 0.0021 972 35.5 0.020 0.16 0.30 0.002 0.0021 0.0056 0.008 0.15 0.0020 < 973 35.5 0.020 0.17 0.30 0.002 0.0024 0.0040 0.019 0.14 0.0018 T 35.52 0.014 0.15 0.20 0.0002 0.0003 0.0024 — 0.13 0.0014 Z U 35.52 0.014 0.15 0.20 0.0002 0.0003 0.0025 — 0.13 0.0035 <r 1 r Table 2—Chemical Compositions of Laboratory (25- and 50-kg) and Mill (60-ton) Heats, Commercial Invar, and Austenitic Stainless Steels Ni C Si Mn P S O Cr Ti N B Note l\ Ti 35.7 0.028 0.16 0.28 0.003 0.0010 0.16 0.028 0.0015 C CQ OD B 35.7 0.021 0.17 0.20 0.003 0.0004 - 0.0035 0.0020 O a LT i t T TiB 35.7 0.030 0.16 0.29 0.003 0.0009 0.16 0.011 0.0013 0.0021 e ro Se QJ Addi JZ .6 SS CR3 36.15 0.018 0.15 0.29 0.004 0.005 0.0051 7.97 0.0030 CR2 36.56 0.016 0.15 0.30 0.004 0.004 0.0075 4.15 0.0014 O C JN c 36.30 0.29 0.005 0.004 0.0033 2.14 0.0021 CR1 0.016 0.15 J?" E o ._- .SP M 35.91 0.015 0.15 3.09 0.003 <0.001 0.0021 0.06 0.0010 •z= \- u- MT1 36.22 0.021 0.15 3.12 0.003 <0.001 0.0018 0.06 1.06 0.0010 "O .
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