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2017<br />
<strong>DVS</strong>-BERICHTE<br />
International<br />
Electron Beam<br />
Welding Conference
International<br />
Electron Beam<br />
Welding Conference<br />
Lectures of the 4 th IEBW Conference<br />
taking place in Aachen on March 21 – 22, 2017<br />
Organized by<br />
German Welding Society (<strong>DVS</strong>), Düsseldorf<br />
International Institute of Welding (IIW), Villepinte<br />
American Welding Society (AWS), Miami
Bibliographic information published by the Deutsche Nationalbibliothek<br />
The Deutsche Nationalbibliothek lists this publication in the Deutsche Nationalbibliografie;<br />
detailed bibliographic data are available in the Internet at http://dnb.dnb.de.<br />
<strong>DVS</strong>-<strong>Berichte</strong> Volume <strong>334</strong><br />
ISBN 978-3-945023-97-6<br />
The lectures are printed in form of manuscripts.<br />
All rights, also for translation, are reserved. The reproduction of this volume or of parts of it only<br />
with approval of the <strong>DVS</strong> Media GmbH, Düsseldorf.<br />
© <strong>DVS</strong> Media GmbH, Düsseldorf ⋅ 2017<br />
Printing: rewi druckhaus, Reiner Winters GmbH, Wissen/Sieg
Welcome<br />
Are you interested in efficient and powerful electron beam welding technology and technological<br />
leadership?<br />
Well, you are at one of the best events in your industry.<br />
The International Electron Beam Welding Conference, IEBW 2017, offers a forum at which<br />
users and manufacturers of electron beam welding and processing technology can meet with<br />
R&D specialists to share their experience and learn about the latest developments in the field.<br />
You get together with like-minded professional people from different sectors of industries<br />
around the world to discuss the latest trends in electron beam technology and gather ideas for<br />
future activities, without the rush of overcrowded trade-shows.<br />
Also, IEBW provides an excellent opportunity for experts not using the electron beam presently<br />
but to getting to know the technical capabilities and advantages of the electron beam. Common<br />
fields where the electron beam is used are for example aircraft and aerospace, automotive and<br />
transportation, shipbuilding and off-shore constructions, rail, nuclear, oil gas and chemical,<br />
military and defense, construction and general fabrication, electronics and medical.<br />
The event is truly one that anyone involved in sophisticated joining challenges should plan to<br />
attend.<br />
Many thanks to International Institute of Welding (IIW), American Welding Society (AWS),<br />
German Welding Society (<strong>DVS</strong>) and Japan Welding Society (JWS), moreover to the sponsors<br />
PTR and SST of Global Beam Technologies, pro-beam and FOCUS and last but not least to the<br />
ISF of RWTH Aachen University and Forschungszentrum Jülich for great assistance and<br />
support.<br />
We are pleased to welcome you to the 4 th International Electron Beam Welding Conference<br />
here in the emperor city of Aachen.<br />
Enjoy your stay in Aachen!<br />
Wilfried Behr<br />
Technical Chairman of Program Committee<br />
and Chairman of <strong>DVS</strong> Working Group<br />
“Electron Beam Welding”<br />
Ernest Levert<br />
Commission IV “Power Beam Processes”<br />
International Institute of Welding (IIW)
Table of contents<br />
Preface<br />
Surface Treatment / Materials<br />
C. Punshon, A. Ferhati, Cambrige/UK, M. Dear and A. Field, Halesowen/UK<br />
Dissimilar metal joining for pressure plant and forge tools ......................................................... 1<br />
M. Okubo and T. Hasegawa, Chiba/JP<br />
Electron beam welding of cast iron and cast steel ..................................................................... 7<br />
S. Valkov, P. Petrov, D. Dechev, N. Ivanov and R. Bezdushnyi, Sofia/BG<br />
Study formation of aluminides in Al-Ti-X (X = Zr, Hf) systems induced by electron-beam<br />
surface treatment ..................................................................................................................... 16<br />
P. Hengst, Freiberg/DE, R. Zenker, Freiberg/DE and Mitweida/DE, T. Süß and K. Hoffmann, Chemnitz/DE<br />
Electron beam profiling and electron beam remelt-bonding for improving the load-bearing<br />
capacity of thermal spray coatings ........................................................................................... 19<br />
Applications<br />
A. Senger, S. Ufer, S. Olschok and U. Reisgen, Aachen/DE<br />
Extension of the material and processing spectrum in wind energy plant through consistent<br />
component safety certificates and welding process optimization ............................................. 27<br />
H. Kendziora, Langenselbold/DE<br />
The diversity of job shop by assistance of the electron beam .................................................. 34<br />
M. Mücke, M. Merkel, Hünstetten-Kesselbach/DE, C. Otten, Aachen/DE, M. Escher, Hünstetten-Kesselbach/DE,<br />
M. Paul, T. Flohr, K. Wrobel, Leipzig/DE, U. Reisgen and I. Balz, Aachen/DE<br />
Advances in micro electron beam welding ............................................................................... 41<br />
Innovations I<br />
A. N. Black, Enfield/US<br />
Electron beam welding of additively manufactured parts ......................................................... 46<br />
L. Halbauer, P. Proksch, A. Buchwalder, Freiberg/DE, and R. Zenker, Freiberg/DE and Mittweida/DE<br />
Using scanning electron beam technology in hard soldering TWIP-matrix composites ........... 52
Innovations II<br />
C. N. Ribton, S. del Pozo, D. R. Smith and W. Balachandran, Cambridge/UK<br />
Design of a plasma cathode electron gun using evolutionary optimization .............................. 58<br />
N. Murray, G. Klimov, A. Beniyash and T. Hassel, Garbsen/DE<br />
Non-vacuum electron beam technology as a universal tool for material processing ................ 65<br />
U. Reisgen, S. Olschok and S. Gach, Aachen/DE<br />
Residual stress reduction by low-transformation-temperature (LTT) filler materials in<br />
electron beam welding ............................................................................................................. 72<br />
Process Diagnostics / Simulation<br />
S. Hellberg, Kassel/DE, S. Ufer, Aachen/DE, S. Böhm, Kassel/DE, and U. Reisgen, Aachen/DE<br />
Influence of fluctuating cathode characteristics on beam quality and welding results in<br />
electron beam welding ............................................................................................................. 78<br />
P. Oving, Metz-Tessy/FR<br />
Development of a new electron beam probing device and analyses method to ensure the<br />
weld quality in time ................................................................................................................... 84<br />
U. Reisgen, S. Olschok, S. Ufer, Aachen/DE, T. Graf and P. Berger, Stuttgart/DE<br />
Observing weld pool dynamics of the vapour capillary by using the real-time polarization<br />
intensity quotient goniometry ................................................................................................... 91<br />
Additive Manufacturing I<br />
G. Klimov, N. Murray, A. Beniyash, Garbsen/DE, A. A. Bataev, O. G. Lenivtseva, Novosibirsk/RU, and<br />
T. Hassel, Garbsen/DE<br />
Additive manufacturing using non-vacuum electron beam technology .................................... 99<br />
S. Janson, B. Loitlesberger, J. Weirather and M. F. Zaeh, München/DE<br />
Improvement of electric charge transportation in metal powders for increased process<br />
stability in electron beam melting ........................................................................................... 104<br />
B. Baufeld, R. Widdison and T. Dutilleu, Rotherham/UK<br />
Electron beam additive manufacturing: Deposition strategies and properties ........................ 114<br />
Additive Manufacturing II<br />
N. Bagshaw, A. Buxton, T. P. Mitchell, V. Jefimovs and M. E. Nunn, TWI Limited, Cambridge/UK<br />
Electron beam wire-fed additive manufacture and distortion control ...................................... 118<br />
B. Klöden, A. Kirchner, T. Weißgärber, B. Kieback, M. Süß, C. Schöne and R. Stelzer, Dresden/DE<br />
Additive manufacturing by electron beam melting – from powder to component ................... 131<br />
List of authors and co-authors ........................................................................................... 137
Dissimilar metal joining for pressure plant and forge tools<br />
C. Punshon, A. Ferhati, Cambrige/UK, M. Dear and A. Field, Halesowen/UK<br />
Transforge aims to show that the fabrication of forged transitions from dissimilar materials can be achieved by<br />
using single-pass electron beam welding followed by re-forging and appropriate heat treatment to develop the<br />
required integrity and properties. This will allow the fabrication of higher quality and higher performance<br />
components for the construction of new nuclear power plant, including newly developing Small Modular Reactors<br />
(SMRs). The spin-off benefit will be in a possible production route for other dissimilar metal joints for use in marine<br />
environments and oil and gas applications as well as for producing forge tools.<br />
Introduction<br />
The use of dissimilar metal joints is prevalent in oil and gas production plant, chemical plant and in the power<br />
generation industries where there are frequent design requirements for materials with combination of corrosion or<br />
oxidation resistance and high strength properties. These are not always readily met by one material without high<br />
cost or the need to compromise. This dilemma can be avoided by employing high strength ferritic or bainitic steels<br />
joined to austenitic or nickel alloy piping systems by dissimilar metal joints and the use of cladding on surfaces of<br />
the high strength, pressure containment plant or components exposed to extremes of temperature and<br />
environmental conditions.<br />
Dating back to the 1940s in the fossil fuelled power sector, dissimilar metal joints are been traditionally produced<br />
through the use of arc welding. In order to minimise the risk of fabrication defects and in-service failures multi-layer<br />
welding or buttering, figure 1, is employed to minimise thermal expansion mismatch, accommodate differences in<br />
hydrogen solubility and reduce the propensity for carbon diffusion, figure 2, in long term service leading to<br />
embrittlement of certain weld interfaces.<br />
Fig. 1 Schematic illustration of buttering in the fabrication<br />
of dissimilar metal joints produced by arc welding<br />
Fig. 2 Narrow region of martensite at dissimilar metal<br />
arc weld interface associated with increased risk of<br />
failure<br />
When considering the fabrication of massive structures such as nuclear power generation plant there are a number<br />
of practical issues which arise due to the necessity to make welds on site. This constraint leads to additional<br />
difficulties in that:<br />
! All-positional, manual welding is necessary, often with restricted access<br />
! Non-destructive testing is more difficult particularly with ultra-sonic testing (UT) as dissimilar metal joints<br />
exhibit varying attenuation, speed of sound and crystallographic differences leading to issues with<br />
interpretation of UT signals<br />
! Post weld heat treatment (PWHT) has to be carried out locally and, rather than achieve stress relaxation,<br />
can induce tensile residual stresses through the differences in thermal expansion coefficients of the<br />
combination of materials.<br />
These issues can be overcome to an extent by the use of so-called “safe-ends” welded to branches or nozzles<br />
during manufacture of vessels allowing simplified field or site welding of the branch connections to pipe work, figure<br />
3. An alternative is to produce a well-characterised transition piece which can be manufactured, heat treated and<br />
<strong>DVS</strong> <strong>334</strong> 1
inspected under controlled conditions and introduced on site allowing similar metal welds to be produced under the<br />
more difficult field welding conditions, figure 4.<br />
Fig. 3 Illustration of safe-end principle fordissimilar metal<br />
joints. (Courtesy of EPRI).<br />
Fig.4 Schematic of pre-manufactured, heat<br />
treated and validated, dissimilar metal<br />
transition piece positioned for site welding.<br />
The aim of the work reported here was first to examine alternative methods for producing dissimilar metal inserts or<br />
transition pieces, which would allow simplified site welding and potentially improved structural integrity and<br />
reliability in service and secondly, to demonstrate the preferred method.<br />
Candidate Materials<br />
Following discussions with potential users of nuclear power plant two material combinations were identified as<br />
appropriate candidates for feasibility testing:<br />
! ASTM SA 508 Gr3 Cl.2 – low alloy quenched and tempered pressure vessel steel<br />
! ASTM B564 2010 N06600 – Inconel 600 nickel alloy used in reactor internals and pipe work<br />
! DGS MS HAS 4304LE – 304 type austenitic stainless steel used in reactor internals and primary circuit<br />
pipework.<br />
In addition, in consultation with the potential industrial users, a typical pipe size where the potential use of<br />
transitions was considered to be attractive was identified as being 364 mm OD by up to 60 mm wall thickness.<br />
Manufacturing Options<br />
A number of processes were considered and a down selection process conducted to define the process most<br />
appropriate for more detailed examination. Although not exhaustive, the basic list is below in table 1:<br />
Table 1. Selection of possible manufacturing methods for dissimilar metal transition joints<br />
Transition joint manufacturing method Considerations<br />
Arc welding Current practice with attendant difficulties due to<br />
number of processes/materials for one joint and<br />
inspection/performance requirements<br />
Solid state welding<br />
Attractive as minimal diffusion but limited by geometry<br />
and overall size<br />
Hot Isostatic Pressing<br />
Attractive with additional benefit of ability to produce<br />
graded composition and thermal expansion properties<br />
– size limited by equipment availability<br />
Additive layer manufacturing<br />
Worthy of study but powder availability and equipment<br />
driven size constraint<br />
Explosive bonding<br />
Well-developed but difficult to inspect and incomplete<br />
bonding common<br />
Power beam welding – laser or electron<br />
beam<br />
Fusion welding with attendant issues of metallurgical<br />
compatibility and missed joint defects<br />
EB Welding in vacuum and<br />
re-forging to produce solid state transition<br />
Not tested but no limit on size or geometry and<br />
examination of feasibility worthwhile<br />
2 <strong>DVS</strong> <strong>334</strong>
On the basis of this rudimentary review, the use of electron beam welding followed by re-forging was adopted for<br />
demonstration of feasibility. This method had been demonstrated already by TWI, Somers Forge and CVE in an<br />
earlier research programme to show the potential of welding similar metals and re-forging. In this work it was<br />
shown that by welding together two hollow part forgings and re-forging it was possible to eliminate any<br />
microstructural evidence that the parts had been welded. The resulting joint was eventually detected using<br />
ultrasonic testing only by virtue of the fact that the average inclusion size and was smaller and inclusions were<br />
fewer in number with more uniform distribution.<br />
Transforge method<br />
The Transforge method was proposed for testing under the Innovate UK initiative for Nuclear Innovation feasibility<br />
competition and awarded funding support.<br />
In essence, the method involves preparation of Monobloc forgings either square or circular in section in different<br />
materials and then joining them together by autogenous EB welding. The weld preparation is a simple machined<br />
square butt joint and EB welding is performed under vacuum thus even when only partially welded the internal<br />
space is evacuated.<br />
Following welding and inspection to confirm sufficient integrity to survive the forging operation the assembly is<br />
heated to the hot forging temperature (~1200 o C) and forged to the required geometry and size. In the feasibility test<br />
the Monobloc forged parts were produced in two sizes, figure 5, viz:<br />
! 175 mm square x 122 mm long<br />
! 175 mm square x 183 mm long<br />
The aim was to machine the rough forged parts to produce regular cuboidal blocks and weld these together to<br />
produce short assemblies of 150mm square x 200mm for later forging into discs and then rings after piecing and<br />
long assemblies of 150mm square x 350mm for later forging into solid discs, figure 6.<br />
150mm<br />
SA 508<br />
Inconel 600<br />
304<br />
350mm<br />
200mm<br />
Fig. 5 Schematic representation of dissimilar metal parts arranged for welding<br />
Fig. 6 Representation of proposed forging reduction to produce discs and piercing followed by mandrel forming to<br />
produce rings<br />
<strong>DVS</strong> <strong>334</strong> 3
Transforge Practical work<br />
Following cleaning, degreasing and assembly the parts were to be EB welded along each edge to produce a deep<br />
penetration weld with either full depth or at least sufficient weld penetration depth to survive the rigours of the<br />
forging process, figure 7.<br />
After welding it was proposed that a shop tool ultrasonic examination be performed to assess weld depth and<br />
integrity. This was carried out using phased array UT from both the ferritic and the austenitic ends of the joints,<br />
figure 8 and readily indicated the weld depth and quality, figure 9. Some selected welds were later sectioned to<br />
assess the reliability of the inspection process which was shown to be good, figure 10.<br />
Fig. 7 As-welded<br />
appearance of dissimilar<br />
metal weld before forging<br />
Fig. 8 Schematic<br />
illustration of method for<br />
phased array UT testing<br />
Fig. 9 Phased array report showing<br />
unfused region (red) in the centre of the<br />
otherwise sound welded dissimilar metal<br />
joint<br />
Inconel 600<br />
A508 steel<br />
Fig. 10 Macro section from EB welded dissimilar metal joint showing partially penetrating EB weld and unfused<br />
central section<br />
The welded dissimilar metal assemblies were subsequently placed in an air furnace, figure 11, and heated to the<br />
proposed forging temperature (~1200 o C) and forged into discs using either the 35cwt hammer forge for smaller of<br />
the two sizes and a 500 ton hydraulic press, figure 12, for the larger parts, figure 13. The smaller discs were hot<br />
pierced and ring forged on a mandrel to produce uniform rings of ~400mm diameter, figure 14.<br />
Finally, after cooling and application of an appropriate conditioning heat treatment using conditions derived by<br />
experiment on small samples, a number of parts were machined to produce complete rings and one sample was<br />
machined with typical arc weld preparation details, figure 15. Some parts were subjected to more detailed UT<br />
testing using TWI’s immersion test system and other samples were sectioned, figure 16, and destructively tested to<br />
assess basic mechanical properties.<br />
4 <strong>DVS</strong> <strong>334</strong>
Fig. 11 Heating<br />
dissimilar metal blocks<br />
to forging temperature<br />
Fig. 12 Forging on 500t<br />
press<br />
Fig. 13 Forged dissimilar<br />
metal discs cooling down<br />
from the forging operation<br />
Fig 14 Forged dissimilar<br />
metal discs and rings<br />
SA 508/IN600<br />
SA 508/304<br />
Fig. 15 Rings machined with<br />
transition piece weld details with<br />
section removed to show position<br />
of dissimilar joint interface<br />
400mm<br />
Fig. 16 Macro sections through forged dissimilar metal discs after heat<br />
treatment and etching<br />
Joint assessment<br />
Whilst this programme was aimed at demonstrating feasibility, and was not intended to be an exhaustive study, a<br />
number of rudimentary mechanical tests were performed on samples removed from the forged dissimilar metal<br />
joints. Cross joint tensile testing, longitudinal and side bend tests, metallography, hardness testing and semi–<br />
quantitative chemical analyses at the interface were performed. The results were generally good with properties<br />
similar to the weakest base metal attained in each case, figure 17 and 18.<br />
Fig. 17 Cross joint (SA 508/304) tensile test specimen<br />
showing failure in the stainless steel with 0.2% proof<br />
strength of 297MPa, UTS 612MPa, El 49% and RA<br />
84%<br />
Fig.18 Longitudinal bend test sample from dissimilar<br />
forged joint between SA 508 and Inconel 600 having<br />
achieved 180 o bend without issue.<br />
<strong>DVS</strong> <strong>334</strong> 5
Concluding remarks<br />
The work described above has demonstrated the feasibility of joining dissimilar metals by EB welding and<br />
subsequent forging. For applications in nuclear power plant, conventional power plant and for use other pressure<br />
containing systems there is more work to do to demonstrate structural integrity and reliable performance under<br />
specific conditions including thermal aging, irradiation, cyclic loading etc. before such joints could be realistically<br />
approved for use. Nevertheless, other applications exist which have less rigorous quality demands where this<br />
technology could be used. One example is in the production of hot work forge tools where Ni alloy/ hot work steel<br />
composite tools could be produced with equivalent performance to Monobloc nickel alloy tools but at significantly<br />
lower cost. It is proposed that this programme is continued to examine the range of materials and applications that<br />
can be addressed in this way and that more property and performance data is obtained for review with the<br />
appropriate classification authorities and code bodies.<br />
Acknowledgements<br />
This work was supported with funding from the Innovate UK Civil Nuclear Innovation competition and the authors<br />
would like to acknowledge the support and advice from many colleagues at TWI Ltd. and Somers Forge Ltd. as<br />
well as industrial guidance from Rolls Royce Nuclear Power and Alstom Power<br />
6 <strong>DVS</strong> <strong>334</strong>
Electron beam welding of cast iron and cast steel<br />
M. Okubo and T. Hasegawa, Narashino/JP<br />
Cast iron and cast steel have high carbon content and the graphite, the selection of welding method has an<br />
important item. EBW, when focusing on the behavior of the graphite has a characteristic of high density energy,<br />
EBW is suitable welding process. In the research on cast iron, Fe-Ni and Ni-Cr filler metals, each of a sheet 0.5mm<br />
thickness, was applied to cast iron of thickness of 18 mm. Under optimal welding processes, weld providing good<br />
welded properties by tensile test and COD test. Using a filler supply system, Ni-Cr of 1.2 mm diameter filler wire<br />
was applied to cast iron of thickness of 6 mm. Under the optimal process conditions and through post weld heat<br />
treatment, the brittle region around graphite in the heat affected zone was decreased. In the research on cast steel<br />
of thickness of 10 mm, the cast steel of about 1.2% carbon content and using materials obtained by adding about<br />
2, 4, 6% Ni. Welding process, in addition to laser welding and manual metal-arc welding were also used. Welds of<br />
cast steel by EBW, it became clear that low cracking tendency compared to laser welding. It was revealed by the<br />
addition of about 2% Ni in cast steel, it is possible to reduce the hardness of the weld metal and suitable structure<br />
control by EBW.<br />
1 Introduction<br />
Cast iron and cast steel are an extensively used for industrial materials. However, the welding charactristic of high<br />
carbon cast iron and steel by convention fusion welding process are poore weldability. Various methods have been<br />
investigated for improved weldability but problem still remain in the field of base metal, filler metal and process<br />
parameters. For welding of cast iron, studies on the selection of filler metal [1,2] have been carried out, and<br />
research on repair welding [3] of cast iron was subjective.<br />
To improve the weldability of cast iron and cast steel, it is necessary to obtained attention to the following factors.<br />
For weld metal, it is necessary to control the formation of cementite caused by dependent on welding thermal<br />
cycle. On the other hand, in the heat affected zone, it is necessary to control the embrittlement structure around the<br />
graphite by diffusion of carbon from graphite.<br />
In the research on spheroidal graphite cast iron,the inside metal welding of nodular graphite cast iron by<br />
continuous casting and filler supply system were examined in investigation of the welding of the higher quality<br />
continuous cast material than sand mold cast material. In the research on spheroidal graphite cast steel, the<br />
objective was to obtain welding conditions without cracking by adding EBW and laser welding by adding 2.0%,<br />
4.0%, and 6.0% of Ni in the base material.<br />
2 Experimental Procedures<br />
2.1 Material and welding conditions<br />
In the study, the developed nodular graphite cast iron as FCD450 according horizontal continuous casting process<br />
was used for main base metal. It presented many advantages over the sand mold cast material such as less<br />
internal defect, a lower area rate of graphite, smaller graphite grain diameter and a higher rate of graphite<br />
nodulation. The inside metal plate are Fe-56Ni, 8Ni-18Cr and filler wire is10Ni-19Cr.<br />
The EBW machine used has the highest output power of 6 kW. The base metal for butt welding was 18mm in<br />
thickness, clamping torque vice, and one pass welding was made. Figure 1 shows process configuration for<br />
welding of inside metal palate. Application of filler wire supply system to nodular cast iron, the filler wire is solid wire<br />
in 1.2 mm diameter. The base metal for filler wire system was 6mm in thickness. Figure 2 shows process<br />
configuration for welding of filler wire supply system.<br />
The base metal is a graphite cast steel to which a graphite promoting element is added to a steel of a<br />
hypereutectoid component. In order to clarify the influence of Ni in the base metal on weldability, Ni was added by<br />
2 to 6%. First, about pig iron and steel materials were melted in a high frequency induction electric furnace, and Ni<br />
2%, 4% and 6% Ni were added in the furnace. As the graphite spheroidizing agent, 2% of Ca - Si is added.The<br />
size of the base metal is 10 (t) x 35 (w) x 28 (L) and the welding length is 35 mm. The microstructure of the base<br />
metals are shown in The microstructure of the base materials are shown in Figure 3.<br />
In study cast steel, there are three types of welding methods: electron beam welding, laser welding and manual<br />
metal-arc welding.<br />
The EBW condition was an accelerating voltage of 150 kV and a beam current of 32 mA, and a welding speed of<br />
1,000 mm / min was selected in order to completely penetrate the base material having a thickness of 10 mm. For<br />
laser welding, CO2 laser welding equipment was used. The welding condition was a beam power of 10 kW, and the<br />
<strong>DVS</strong> <strong>334</strong> 7
welding speed was selected to be 1500 mm / min in order to completely penetrate the base material with a<br />
thickness of 10 mm.<br />
For the manual metal-arc welding, a power source of AC arc characteristic was used. In the welding operation, a<br />
U-shaped groove portion was machined on the surface of the base material. The depth of the groove was 7 mm<br />
and the width was 14 mm. Welding is hand welding and construction with four layers. The coating welding rod had<br />
a composition of D308 (19Cr-10Ni), the welding current was 180 A, and the welding speed was 60 mm / min. The<br />
inter-pass temperature was 423 K.<br />
Fig. 1. Welding of inside metal plate procedure.<br />
Fig. 2. Welding of filler wire supply procedure.<br />
8 <strong>DVS</strong> <strong>334</strong>
2.2 Evaluation of welded joints<br />
In case of cast iron, observation of defects in welds and measurement of the penetration was made of the cross-section<br />
of welds. Micro Vickers hardness test was performed on the cross section. Next, with optimal welding condition chosen,<br />
tensile test, impact test, COD test, analysis of chemical components of fusion zone, and EPMA analysis of welds.<br />
In case of cast steel, crystallization tendency, hardness measurement and morphology of electron beam weldability, laser<br />
weldability and manual metal-arc welded zone were observed by adding 2 to 6% Ni to graphite cast steel.<br />
Fig. 3. The microstructure of the cast steel.<br />
3 Results and discussions<br />
3.1 Welding of cast iron<br />
3.1.1 Welding of inside metal plate procedure<br />
(1) Prevention of defects<br />
In the welding of the cast iron, the selection of the filler metal and the welding heat source is to be important. With<br />
the beam current changed at two levels of 30 and 40mA, welding speed at three levels of 450,500 and 550<br />
mm/min and active beam parameter of for levels at 0.8, 0.9, 1.0 and1.1, the forms of the bead cross-section were<br />
observed. Both Fe-Ni and SUS304 showed, under the condition of the beam current at 30mA, with the active beam<br />
parameter at 0.8, wedge type; at 0.9 well type; at 1.1, wedge type.<br />
<strong>DVS</strong> <strong>334</strong> 9