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Modification of the grain structure of austenitic welds for improved ultrasonic inspectability
S. Wagner, S. Dugan, S. Stubenrauch, O. Jacobs
MPA Universität Stuttgart
38th MPA-Seminar October 1 and 2, 2012 in Stuttgart
476
Abstract
Austenitic stainless steel welds, which are widely used for example in nuclear power plants
and chemical installations, present major challenges for ultrasonic inspection due to the grain
structure of the weld. Large grains in combination with the elastic anisotropy of the material
lead to increased scattering and affect sound wave propagation in the weld. This results in a
reduced signal-to-noise ratio, and complicates the interpretation of signals and the
localization of defects. The aim of this project is to influence grain growth in the weld during
the welding process to produce smaller grains, in order to improve sound propagation
through the weld, thus improving inspectability. Metallographic sections of the first test welds
have shown that a modification of the grain structure can be achieved by influencing the
grain growth with magnetic fields. For further optimization, test blocks for ultrasonic testing
were manufactured to study sound propagation through the weld and detectability of test
flaws.
1 Introduct ion
1.1 Motivation
For pressurized components operating at high stresses and at high temperatures, the
integrity of the welds is critical for a safe and reliable operation. In the nuclear industry,
(petro-) chemical industry, and also in conventional power plants at higher temperatures,
austenitic welds are widely used. Non-destructive testing is an integral part of the quality
assurance for these welds during the manufacturing process and in-service inspections. For
volumetric inspection and inspection of non-accessible inner surfaces, ultrasonic testing or
radiography can be used. In many cases, ultrasonic testing is the preferred method due to
large wall thickness, limited accessibility, or cost considerations.
The challenges facing ultrasonic testing of austenitic welds result from elastic anisotropy of
the material in combination with the grain structure of the weld. As long as the grains are
randomly oriented and sufficiently small compared to the acoustic wavelength, the anisotropy
of the material does not affect the acoustic properties on a macroscopic scale. Austenitic
welds, however, consist of large grains that are oriented depending on the cooling conditions
during the welding process – so-called dendrites, or dendritic structure, Figure 1. An example
for an austenitic stainless steel weld with distinctly dendritic crystals is shown in Figure 2.
This inhomogeneous, anisotropic structure of the weld strongly affects ultrasound
propagation. The following effects can be observed: local variations in the sound velocity,
deviation from propagation direction expected for isotropic material, scattering at grain
boundaries and at the fusion line, mode conversion. In addition to a decrease in signal-to-
noise ratio, this leads to difficulties for the interpretation of ultrasonic signals with respect to
localization and sizing of defects, and the distinction between reflections from real defects
and false indications.
477
The diff
number
develop
The aim
welding
be achi
dendritic
1.2 C
To avo
approac
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Figure
ficulties with
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ieved by cr
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Current sta
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however, t
1: Schemati
h ultrasonic
h projects,
e improvem
oject presen
n order to im
reating a m
s.
ate of rese
ove-mention
ving modif
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d design to
has lead
this type of
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Figure 2: a
c inspection
for example
ment of ultras
nted here is
mprove the
more fine-gr
earch and
ned difficul
ications du
al modificat
improve ac
to improve
f weld geo
owth of dend
austenitic we
n of austen
e: [1], [2], [3
sonic inspe
s to influenc
accoustic p
rained micr
technolog
lties for ul
uring the
ions, such
ccessibility
ements con
ometry can
rites. The nu
eld with distin
itic welds h
3] and othe
ection and s
ce the grain
properties o
rostructure,
gy
ltrasonic in
manufactur
as reducin
of the weld
ncerning u
result in v
ucleation star
nctly dendritic
have been t
ers. Most of
ignal analys
growth in t
of the auste
which mea
nspection, t
ring proces
ng the volu
for the insp
ltrasonic in
very long g
rt at the fusio
c structure
the target o
f them deal
sis techniqu
the weld du
nitic weld. T
ans less di
there are
ss. One o
ume of the
pection. Th
nspection. I
grains (thro
on face of the
of a high
with the
ues.
uring the
This can
istinctive
different
of these
weld or
e use of
In some
ugh-wall
e weld
478
extension) in the center of the weld which cause a reflection of the ultrasonic pulse
comparable to an interface reflection [4], [5].
The second type of approach is based on efforts to influence the microstructure of the weld
during the welding process, i.e. the solidification of the weld material. The possibility of
influencing the microstructure in order to create finer grains by the aid of electromagnetic
fields or ultrasound has been demonstrated in different research projects.
1.2.1 Impact of electromagnetic fields
Effects of alternating electromagnetic fields on the liquid state of an aluminum, austenitic
material, on a model liquid (Ga-In-Si-alloy), and on a Ni-based alloy are described in the
literature [6], [7], [8], [9]. Each of these studies was conducted in a laboratory set-up using
melting pots. Grain refinement was observed due to the electromagnetic stirring of the liquid
melt.
Other publications report on the use of magnetic fields to modify the arc during plasma
welding [10], or to influence the laser weldung process for high-alloyed steels [11] or
aluminum alloy [12].
1.2.2 Impact of Ultrasound
High power ultrasonic waves applied to a liquid metal have been described as grain-refining
[13]. In [14] ultrasonic treatment of solidified weld layers of an austenitic low carbon steel was
shown to produce a finer microstructure as well as improved mechanical properties (yield
strength, micro hardness).
1.2.3 Impact of Modifications of the Welding Process
Another method of influencing the microstructure of a weld is to modify the welding process
itself. Leading manufacturers of welding equipment experiment use approaches based on a
reduction of heat input into the component during welding, such as EWM’s “coldArc”
Technology [15] and the CMT-Technology developed by Fronius. With these “cold” welding
processes, significantly shorter cooling times of the weld and modified microstructures can
be achieved.
2 Full Description of the current study
The survey of existing literature has shown that research on methods for modifying the grain
structure of austenitic welds by influencing the welding process is rather limited. Application
of magnetic fields near the arc appears to be the most promising tool to influence the
microstructure. These magnetic fields can be static or fluctuating. In this investigation,
magnetic fields, as well as a modification of parameters for the welding process are applied.
479
2.1 E
Electrom
growth
melt and
detachm
of grain
improve
For the
automa
impleme
with the
(Figure
With thi
1.4432)
investig
The mo
100 Hz
metallog
pass. T
significa
Figu
varia
Experimen
magnetic fie
of dendritic
d causes lo
ment of den
n growth is
ement of we
e applicatio
ted TIG-w
ented. The
e TIG-elect
5).
is experime
) were crea
gations the w
ost significan
z for the
graphic sec
The dendrite
antly reduce
ure 3: Schem
ations in chem
nts using
elds result i
c structures.
ocal variatio
ndrite tips, c
influenced
elding seam
on of a pu
welding sys
electromag
rode at con
ental set-up
ated, applyi
welding fille
nt changes
applied ma
ction of the
es appear
ed.
matic represe
mical compo
magneti
n a modified
. The magn
n in the con
creating new
by the mag
m quality can
ulsed mag
stem equi
gnet was loc
nstant spee
, several m
ing pulsed
er material S
in the struc
agnetic fiel
test weld.
finer and s
ntation of the
sition within
ic fields
d heat trans
neto-hydrod
ncentration
w sources
gnetic field
n be observ
netic field
ipped with
cated below
ed and a c
multi-pass b
magnetic f
SAS 4-IG w
cture of den
ld. Figure
The orienta
shorter. Gro
e detaching o
the weld cau
sfer in the li
ynamic effe
of the alloy
for nucleat
and can the
ved [12], [16
under rea
h an elec
w the weld ro
constant dis
utt welds o
fields at dif
as used.
ndrites were
6 shows
ation of den
owth over s
of dendrites
used by mag
quid melt w
ect creates
ying elemen
ion (Figure
erefore be
6].
alistic weld
ctromagnet
oot and mo
stance of 4
f 16 mm th
fferent puls
e achieved
a photogra
ndrites chan
several wel
tips due to c
gnetic fields (
which influen
a current w
nts. This can
3). The or
influenced.
ing conditi
(Figure
oved simulta
mm from
hick plates (
se rates. Fo
with a puls
aph of an
nges for ea
d passes c
currents and
(S: solid; L: li
nces the
within the
n lead to
ientation
Also an
ons, an
4) was
aneously
the root
(material
or these
e rate of
etched
ach weld
could be
local
iquid)
480
2.2 Ex periments with Influencing the TIG arc
The second technique for influencing the solidification process of the weld used in this study
was the application of a pulsed TIG arc. Figure 7 shows the weld seam which shows the
most significant changes in microstructure obtained with a pulsed TIG arc.
Figure 6: Austenitic weld, welded under influence of an
electromagnetic field, pulse rate of f = 100 Hz
Figure 4: Automated TIG-welder with TIG-
electrode, filler wire feeder, electromagnet, and
test plate with weld seam preparation
Figure 5: Detail of electrode and electromagnet
481
In order to exclude a possible influence of grain structure in the root passes on the formation
of dendrites in the filler weld passes, the geometry of the weld seam preparation was carved
out of the test plate using spark erosion. The photo of the etched metallographic section
(Figure 7) shows a more fine-grained structure of the first filler weld pass compared to a weld
with hand welded root pass (see Figure 6).
2.3 Ex periments with different interpass temperatures
In order to investigate the influence of interpass temperature Tip on the formation of
dendrites, experiments with minimum interpass temperature (room temperature RT), with the
maximum recommended interpass temperature, as well as significantly excessive interpass
temperatures (210 °C – 245 °C) have been performed. For the austenitic Cr-Ni(Mo)-steel
used here, it is recommended not to exceed Tip = 150°C [17].
For the weld seam welded at minimum Tip (RT, Figure 8), the grain structure is almost
identical to the structure for the weld without modifications in the welding process (welded at
Tip ≦ 150°C). For the maximum interpass temperatures, growth of dendrites through several
weld passes can be observed, Figure 9. This can be explained by the higher content of heat
stored in the material due the high interpass temperatures, allowing an extended grain
growth in one preferred direction, and resulting in larger grains of one particular orientation.
Figure 7: Manual TIG-weld, pulsed TIG-arc at 100 Hz, weld seam
preparation by spark erosion, no root gap
482
2.4 Ultrasonic Testing of Influenced Welds
For the first trial of ultrasonic testing of the different welds, test blocks were manufactured
from one non-modified weld (SN17, welded with standard parameters), three pulsed arc
welds (SN 18 - 20), as well as the weld with minimum interpass temperature (SN22). A side
drilled hole (SDH) with a diameter of 1,5 mm was drilled in the center of the weld as a test
reflector (Figure 10). All test blocks have identical geometries.
All test blocks were inspected by mechanized ultrasonic phased array testing, using shear
waves at a frequency of 2.25 MHz, at different angles of incidence. The aim of the
inspections was to analyze the influence of the microstructure on the sound propagation
through the weld. For a better sound propagation a better flaw detectability can be expected.
The influences of the microstructural modifications (SN18 - SN22) are compared with
acoustic characteristics of the non-modified weld (SN17).
Figure 8: Manual TIG weld with minimum Tip. (RT) Figure 9: Manual TIG weld with too high Tip.of 245°
Figure 10: US-test block with side drilled hole in the center of the weld (SN20)
483
Table 1 shows the B-scan projection images (side view) of the phased array inspection for
the 2.25 MHz shear wave with an angle of incidence of 70 °. For a better comparability only
the manual TIG welds with the weld seam preparation by spark erosion are shown.
Table 1: Phased-Array B-scans of test blocks
Type of weld B-scan for 70° angle Macrosection
SN17:
No modification
SN18:
Pulse of light arc
100Hz
SN19:
Pulse of light arc
50 Hz
SN20:
TIG 500 Hz,
SN22:
Min. Interpass-
Temperature
484
For the test blocks SN18 – SN20, obtained with different pulse frequencies of the TIG arc,
the evaluation of the B-scans shows variations in the acoustic characteristics of the welds. It
appears that for low frequencies a better detectability of the defect is achieved. For higher
frequencies the signal-to-noise ratio decreases and a higher noise level due to scattering
from the microstructure of the weld can be observed.
Test block SN22 was welded with the minimum interpass temperature, allowing the weld
beads to cool down to room temperature. It was expected to obtain an improved
microstructure, resulting in improvements in the acoustic properties. This expectation was
confirmed neither by ultrasonic inspection nor by metallography.
SN17, the non-modified test block, shows the characteristic grain structure of austenitic
welds. According to the geometric characteristics of the sound beam the B-scan shows a
good correlation with the theoretical image of the scan, except for the localization of the
defect.
Further ultrasonic inspections are currently carried out in order to verify these first
experimental results and interpretations.
3 Summary and conclusion Metallographic examinations show an influence on the growth of dendrites due to
electromagnetic fields and pulsation of the TIG arc with varying frequencies during the
welding process. Evaluation of the microstructure of electromagnetically influenced welds
leads to the assumption that for low frequencies (approx. 100 Hz), the strongest
modifications of the dendritic structure can be achieved: Significant changes in the
orientation of dendrites, more fine-acicular grains are observed, and a growth through
several weld passes could be avoided. The assumption that this also leads towards
improved acoustic characteristics for ultrasonic inspection has yet to be verified.
For the modification of the light arc the following results can be observed: For pulsed arcs
with low frequencies, microstructures with short dendrites with different orientations can be
produced. The experiments show a fine-grained area in the first weld pass. The influence of
nucleation from the root pass structure could be avoided by carving the weld geometry out of
a plate, thus creating a weld without a root.
For optimization and evaluation of influencing parameters, ultrasound propagation
experiments were performed using ultrasound test blocks with reference flaws (1,5 mm
SDH). By studying ultrasonic propagation through the weld, influences on the acoustic
properties of the usually anisotropic welds can be observed. The first results of ultrasonic
inspection lead towards the assumption, that for lower pulse frequencies an improved sound
transmission can be obtained.
485
An impact of a reduced interpass temperature on the growth of dendrites could not be
observed. Also, the maximum applied interpass temperature in the range of 210 °C – 245 °C
did not show significant changes in the microstructure. Ultrasonic inspections of these welds
are currently under way.
Further studies considering the effects of high power ultrasound on the solidification and
grain growth in the weld will also be conducted as within this research project.
References
[1] Williams, P. (1976). Ultrasonic testing of austenitic steels (a selectiv bibliography
1958-1975). (Bd. Bibliography 252). London: Central Electicity Generating Board.
[2] Neumann, E. et al. (1995). Ultraschallprüfung von austenitischen Plattierungen,
Mischnähten und austenitischen Schweißnähten (Kontakt & Studium), Bd. 377.
Expert-Verlag.
[3] Just, T., Kuhlow, D., Matthies, K., Römer, M. (1978). Über den Stand der
Entwicklungen einer Ultraschallprüpftechnik für austenitsiche Schweißverbindungen
(Schweißen in der Kerntechnik Ausg. Nr. 52). Hamburg: DVS-Berichte .
[4] Schmid, R. (1995), Ultraschallprüfung von austenitischen Plattierungen, Mischnähten
und austenitischen Schweißnähten, Eberhard Neumann (Hrsg), Expert-Verlag,
(Kontakt und Studium) Bd. 377, Kapitel 4
[5] „Prüfbarkeit von dickwandigen Bauteilen aus Nickellegierungen und
Schweißverbindungen mit zerstörungsfreien Prüfmethoden“ gemeinsamer
Abschlussbericht der Forschungsstellen BAM Berlin, IZfP Saarbrücken, MPA
Stuttgart zum Vorhaben COORETEC TD-1 (unveröffentlicht)
[6] Lu, D. (2007). Refinement of primary Si in hypereutectic Al–Si alloy by
electromagnetic stirring. Journal of Materials Processing Technology, p. 13 - 18.
[7] Gao, Y.-L. (2004). Comparative study on structural transformation of low-melting pure
Al and high-melting stainless steel under external pulsed magnetic field.
Materialwissenschaft und Werkstofftechnologie, p. 385 - 395.
[8] Wang, X. D. (2005). Two kinds of magnetic fields induced by one pair of rotating
permanent magnets and their application in stirring and controlling molten metal
flows. Journal of Crystal Growth, p. e1473 - e1479.
[9] Jin, W. (2008). Grain refinement of superalloy IN100 under the action of rotary
magnetic fields and inoculants. Materials Letters, p. 1585 - 1588.
486
[10] Cheng, J. (August 2008). Effect of electromagnetic stirring on the microstructure and
wear behavior of iron-based composite coatings. Journal of University of Science and
Technology Beijing, Number 4, p. 451.
[11] Berger, P., & Graf, T. (2008). Gestaltung und Kontrolle des Nahtdurchhangs beim
Schweißen. Forschungsvorhaben IFSW Universität Stuttgart, IGF-Vorhaben
14.959N.
[12] Lindenau, D. (2006). Magnetisch beeinflusstes Laserstrahlschweißen (Bd.
Dissertation IFSW Universität Stuttgart). München: Herbert Utz Verlag GmbH.
[13] Zhang, Z. (Feb. 2009). influence of high-intensity ultrasonic treatment on the phase
morphology of Mg-9.0wt%Al binary alloy. Rare Metals, p. 86.
[14] Gust, W. (1999). ultrasonic shock treatment of welded joints. Materials Science, p.
678 - 683.
[15] Kocab, H. (2010). Neue Lichtbogenform für hohe Wirtschaftlichkeit und Nahtqualität.
Schweißen im Anlagen- und Behälterbau, Sondertagung München, S. 40 - 46.
[16] Kern, M., Berger, P., Hügel, H. (2000) Magneto-Fluid Dynamic Control of Seam
Quality in CO2 Laser Beam Welding. Welding Journal, p. 72-s – 78-s
[17] Böhler-Handbuch “Wissenswertes für den Schweißer” Ausgabe 09/ 2010, Böhler
Schweißtechnik Austria GmbH
487