n O P T O R AT T H F ^ K
Validation of Models for Welding and
Post Weld Heat Treatment in Product
Development of Aerospace Components
Daniel Berglund
Department of Applied Physics and Mechanical Engineering
Division of Computer Aided Design
Components
Daniel Berglund
2003
Division o f Computer Aided Design
Department of Applied Physics and Mechanical Engineering
Luleå University of Technology
SE-971 87 Luleå, Sweden
danielb@cadduth.se
Academic thesis for the degree of Doctor of Philosophy, which with the due permission o f the
Faculty Board at Luleå University of Technology w i l l be defended in public, in room E632,
Studion E-house, Wednesday the 10
t hof December 2003 at 09.00.
External Examiner: Associate Prof. P. Michaleris, Department of Mechanical and Nuclear
Engineering, Pennsylvania State University.
continued at Volvo Aero Corp the last three and an half years. I have been financed by Volvo Aero
and NFFP
1during the whole time of my research which I am very grateful for. It has been a
fantastic opportunity to concentrate on a specific research area during such a long time and I have
many people to be thanked.
First of all I would like to thanks my supervisor, Lars-Erik Lindgren for all his advice, comments
and enthusiasm regarding my work. I would like to thank my colleagues at Computer Aided
Design and at the department of Advanced Manufacturing Process Development at Volvo Aero.
Peter Jonsson for his support in the beginning of the project and Henrik Runnemalm support
especially as a good friend.
A special thanks to my friend and college Henrik Alberg, who I have really enjoined working
with. We have had a lot of interesting discussions both regarding work and other important issues.
Finally, I would like to thank my fiancé Malin, you have been tremendous patient and supported
me, / love you.
achieved by finding a stable process-parameter window for each manufacturing operation and to
choose an order of manufacture, which gives an adequate result. Production planning has
traditionally been carried out from experience and experiments. However, in order to reduce
lead-time and cost, computer based numerical simulations using the finite element method is
increasingly being used. Simulations can give valuable information about component dimensions,
shape, and residual stresses after each manufacturing process. The generated stresses and
deformation at each individual manufacturing step affect the subsequent operation. One example is
welding where stresses are generated in the structure and the level of stress is dependent on the
type of fixture. I f the fixture does not allow the component to move during the operation, then
large residual stresses are generated but the deformations are small. Some of these stresses are
released when the component is taken out of the fixture and others are released when it is
heat-treated. This is one example why production must consider the whole manufacturing chain.
Using combined welding- and heat treatment simulation in the early stages of product
development require a tool, which give result of sufficient accuracy and simulations completed
within an acceptable time. The necessary conditions to f u l f i l the accuracy requirement are dealt
with in this thesis. Both geometrical- and material simplifications are investigated and conclusions
about the effect on full-scale components are drawn.
Before the simulation tool with its simplifications is used in product development, the models have
to be validated. Validation of tools used for manufacturing simulations on component level must
be minimised because of the cost and limited time. A two-stage validation strategy for welding and
post weld heat treatment models is presented. It can be performed in the pre-development stage or
even before a product is planned, and thereby reduces the time needed when simulations w i l l be
used in later stages. The material model is validated separately using a simple experiment
executing the relevant phenomena. In the second validation step, the models for welding and heat
treatment are validated on a test plate using the deformation and residual stress as validation
parameters.
This dissertation includes an introduction and the following papers:
I . D. Berglund, L.-E. Lindgren, A . Lundbäck, Three-Dimensional Finite Element
Simulation of Laser Welded Stainless Steel Plate, Proc: 7
t hInt. Conf. On Numerical
Methods in Industrial Forming (NUMIFORM), Japan (2001), 119-1123.
I I . D . Berglund, H. Runnemalm, Comparison of Deformation Pattern and Residual Stresses
in Finite Element Models of a TIG-welded Stainless Steel Plate, Proc: 6
t hInt. Conf.
Trends in Welding Research, USA (2002), 826-831.
III. D. Berglund, H . Alberg, A two-stage Approach for Validation of Welding- and Heat
Treatment Models used in Product Development, to be published.
IV. D. Berglund, H. Alberg, H . Runnemalm, Simulation of Welding and Stress Relief Heat
treatment of an Aero Engine Component, Finite Element in Analysis and Design, Vol 39
(2003), 865-881.
V. H . Alberg, D. Berglund, Comparison of Plastic, Viscoplastic, and Creep Models when
Modelling Welding and Stress Relief Heat Treatment, Accepted at Computer method in
P R E F A C E
A B S T R A C T
D I S S E R T A T I O N
1. I N T R O D U C T I O N 3
L I Background 3
1.2 A i m and Scope of present research 4
1.3 Approach 4
1.4 Manufacturing simulation in product development 4
1.5 Welding in the aerospace industry 5
1.6 Heat treating of metals 6
2. M A T E R I A L A S P E C T S IN W E L D I N G AND H E A T T R E A T M E N T S I M U L A T I O N S . . 9
2.1 Microstructure behaviour and thermal dilatation 9
2.2 Transformation Induced Plasticity (TRIP) 11
2.3 Rate dependent plasticity and creep 12
2.4 Material model in welding and quenching analysis 14
2.5 Material model during stress relief heat treatment 15
3. S I M U L A T I O N O F W E L D I N G 17
3.1 Simulation models in finite element analysis 17
3.2 Heat input model 19
3.3 Joining of material and treatment of filler material 19
3.4 Influence of initial geometry 20
4.2 Cooling sequence 23
5. V A L I D A T I O N O F S I M U L A T I O N M O D E L S 24
6. S U M M A R Y O F PAPERS 28
6.1 Three-Dimensional Finite Element Simulation of Laser Welded Stainless Steel Plate (Paper
I). 28
6.2 Comparison of Deformation Pattern and Residual Stresses in Finite Element Models of a
TIG-welded Stainless Steel Plate (Paper II) 28
6.3 A two-stage approach for validation of welding- and heat treatment models used in product
development (Paper III) 28
6.4 Simulation of Welding and Stress Relief Heat Treatment of an Aero Engine Component
(Paper I V ) 29
6.5 Comparison of plastic, viscoplastic, and creep models when modelling welding and stress
relief heat treatment (Paper V) 29
7. DISCUSSION AND C O N C L U S I O N S 30
8. S C I E N T I F I C C O N T R I B U T I O N 32
1. Introduction
1.1 Background
A large number o f the components in the aerospace industry are complex shaped and
manufactured in high strength material. The tolerance requirements on the dimension and the
shape are often rigorous. The manufacturing of such components is therefore limited to a number
of processes. One major choice is whether the components should be a casting or a fabrication. In
a fabricated structure, the individual parts can be castings but the main structure is created by
assembling different parts to a larger structure. A fabricated structure has a number of advantages
in comparison with large castings. It is for example possible to choose different material for
different parts o f the structure, the minimum thickness is not restricted. Furthermore, the design of
the component is more flexible and the number of potential subcontractors for incoming material
is not limited to only a few companies. The disadvantage is that the manufacturing processes
require a large number of operations and that joining operations such as welding generate
unwanted stresses and deformation.
The generated stresses and deformation at each individual manufacturing step affect the
subsequent operation. One example is welding where stresses are generated in the structure and the
level of stress is dependent on the type of fixture. I f the fixture does not allow the component to
move during the operation, then large residual stresses generated but the deformations are small.
Some of these stresses are released when the component is taken out of the fixture and others are
released when it is heattreated. The accompanying distortion may be so large that the tolerance
requirements after heat treatment are not fulfilled. However, i f the fixture is too loose, then the
deformations during welding will already be unacceptable large. This is one example why the
whole manufacturing chain has to be considered when designing an fabricated structure. More
planning is required for a fabricated stmcture than a large casting because of the larger number of
manufacturing operations involved. The decisions to be taken when a new product is going to be
manufactured are often based on knowledge from earlier projects and from experiments on
simplified components. This requires people with long experience and sufficient development
time. Reducing the lead-time in this process requires efficient simulation tools for prediction o f the
effects of the manufacturing chain. It is possible to use results from these simulations to estimate
the lifetime of a product and thereby also be used for design ofthe product.
1.2 Aim and Scope of present research
The objective of the work presented in this thesis is to find how to use the finite element method
for combined welding and heat treatment simulations in product development. The simulations
will be used for designing and planning the manufacturing processes in order to obtain an
acceptable final shape of the component and a robust manufacturing process. The research
question is formulated as:
How are models of combined welding- and heat treatment giving adequate accuracy created to
support design for manufacturing in the early stages of product development?
The term modelling is in this thesis the preparation of a symbolic device built to simulate and
predict certain aspects of the behavior of a system. Running the symbolic device, in this case a
FE-program is the definition of simulation. Large FE-models are computational demanding for
simulations o f the manufacture of components with complex shape. The result of the simulation
must be o f sufficient accuracy and completed within an acceptable time i f manufacturing
simulations are going to be used in product development. This requires geometrical
simplifications, correct modelling of the boundary conditions and a correct material behaviour in
each process. The validation of the simulation models is therefore another important issue
discussed in this work.
In this thesis, adequate accuracy is the level of result that gives qualitatively correct results and
makes it possible to compare different solutions and describe a general behaviour. Sudnik et al. [1]
have given the following definition of an adequate model. The necessary simulation accuracy must
be defined on the compromise between complexity and accuracy of the physical-mathematical
model. Such an optimised model is termed adequate model. The term acceptable time has a unique
meaning depending on industry and application. In the aerospace industry, a simulation time of
one to a number of days may be an acceptable simulation time.
The processes of interest in this work are arc/beam welding and stress relief heat treatment in gas
cooled vacuum furnaces. These are common in the aerospace industry. Only single pass welding is
studied and the global deformation during the processes is in focus. The material of the studied
objects is limited to one material, a martensitic stainless steel. An effort is made to support the
early stages of product development where different product and process concepts shall be
compared.
1.3 Approach
The work is carried out in close co-operation with participating industry and the research result is
used and evaluated in demonstration projects. The research is performed using both real
components and simplified stmctures. A commercial finite element program is the base tool and a
deductive research approach is used. Known technologies are tested and the limitations of these
models and techniques are investigated when used in welding and heat treatment applications.
1.4 Manufacturing simulation in product development
The finite element method (FEM) has frequently been used by design engineers to calculate
deformation and stresses for the functional analysis. This analysis gives for example stresses and
deformation due to in-service loads. The tools have been developed to support analysis of the
components performance but not for predicting the effect of manufacturing on components. To
develop efficient tools, supporting the evaluation of manufacturing effects, a number of research
issues have to be dealt with. The topics range from design and manufacturing methodology to
constitutive relations of materials and numerical algorithm for solution of equation systems. The
product development of a component, not only in the aerospace industry, can be divided in a
number of phases for both design and manufacturing, see Figure 1. Manufacturing simulations can
be used as a support tool in all phases of the product development. It works both as channel for
communication between design and manufacturing and as a tool for manufacturing engineers to
evaluate different manufacturing sequences (manufacturing planning).
Pre-development
Validation of
simulation tools
Product
Requirements
f
Tools for functional evaluation
)
Concept
Design
Preliminary
Design
Detailed
Concept
Design
—Preliminary
Design
L>Design
i r
Iff
i r
Tools for evaluation of manufacturing effects
1
J l
Inventorv of
Preliminary
^
Detailed
known methods
preparation
Preparation
Tools for planning of manufac turing
y17
Figure 1. Tools and preparation stages in product development.
Because of the requirements of low cost and effective product development, developing
manufacturing processes and simulation tools during product development is strictly limited due to
the short development time.
Validation of tools used for manufacturing simulations cannot be performed on component level
because o f the cost, time and the problem of finding model errors. Validation of simulation models
for manufacturing processes has to be done before the tool can be used as a qualified tool in
product development. The main objective in this thesis is to find suitable models to be used in the
concept design phase and to define a validation approach for thermo-mechanical models in
general.
1.5 Welding in the aerospace industry
The most common welding processes in the aerospace industry are Gas Tungsten Arc Welding
(GTAW), Electron Beam Welding (EB), Laser welding and Friction welding. In the
GTAW-process is the heat produced by an electric arc between a non-consumable tungsten electrode and
the workpiece. An inert gas, argon or helium is used as a shield for corrosion of the weld zone and
the electrode. Filler material can be used and is then added from the side, see Figure 2.
Figure 2. Schematic figure ofthe GTAW-process with external added filler material.
Gas tungsten welding is best suited for welding material with thickness between 0.5 and 3 mm.
Electron beam welding is a method where a concentrated electron beam with a high power
density is used to melt the material. Therefore, the fusion zone is small and the penetration depth is
large. EB has also the advantage o f giving small residual deformation o f the workpiece. It's a
method well suited for butt-welding in thick material, up to 250 mm. The welding operation has to
be done in a low-pressure environment to reduce the retardation of the electrons.
Laser welding is also a method that produces a high energy density beam but the energy source
is a light amplifier. The advantage of laser welding in comparison with EB-welding is that there is
no need for a low-pressure environment and the light can easily be transported from the light
source to the work piece by mirrors or by optical fibre. The most common types for welding is
C O 2 - and Nd:YAG-lasers where the light from the Nd:YAG can be "transported" in an optical
fibre. This is not the case for the C0
2-lasers where mirrors have to be used but the method has the
advantage of producing a laser beam with a higher power than in the Nd: YAG-case. Laser welding
is most effective for thin plate applications.
Friction welding does not give a complete melted zone between the individual work pieces. Heat
is generated between the parts due to friction. The applied pressure is removed when the desirable
temperature has been reached. There are a number of procedures for this weld method. One
example is friction welding by using two rotational parts where one of the parts is put in contact
with the other by using a hydraulic cylinder. Friction stir welding is another method where a
consumable rotated tool is pressed onto the workpiece in the same time as the tool is moving along
the butt joint.
1.6 Heat treating of metals
The material in aerospace applications is often chosen because of their heat and corrosion
resistance, fatigue properties and low weight. Depending on the base material of the component,
the heat-treating is done at different temperatures and holding times. In order to describe a number
of common heat treating processes and their purpose, steels are used as an example. Steel is
defined as an alloy o f iron and carbon with the carbon content up to about 2 w t % [2]. Other alloy
elements can be up to 5 wt% in a low-alloy steel and more in a high-alloy steel. Heat treatment is a
general name of a large number of thermal processes where the goal is often to obtain a
satisfactory hardness. Figure 3 shows typical heating ranges in an Iron-Carbon diagram for
different heat treating processes. A\ is the eutectoid line, or the lower critical temperature for
austenite transformation and A
3is the upper critical temperature. A
c mrepresent the upper critical
temperature for hypereutectoid steels (Steels with more than 0.77 w t % C). The most common
heat-treating processes for steels are described below.
Normalizing
912
727
400
Full Annealing
Tempering
Stress Relief Heat Treating
Figure 3. Iron-Iron Carbide phase diagram showing typical temperature ranges for different heat
treatment operations.
Annealing is a heat treatment process, refers to a material exposed to an elevated temperature
(above the A3 temperature) for an extended period of time, and thereafter cooled down. This is
primarily done in order to soften the material. Ferrite and pearlite are the dominating phases in the
material after the annealing process. I f the cooling rate is increased, then martensite w i l l be
created, this process is called quenching. The hardness of the material is controlled by the amount
of martensite created. The cooling rate and thereby the amount of martensite can be controlled by
the selection of quench medium. Common quench media is water, saltwater, oil, polymer solution
or some inert gas (helium, argon or nitrogen).
Tempering of steel is a process in which previously hardened or normalized steel is heated to a
temperature below the A]-temperature in order to increase ductility and toughness. The difference
between tempering and stress relief heat-treating is that the aim of the tempering operation is to
create a certain microstructure. In the other case, the primary aim is to relieve stresses, but both
procedures are performed in the same temperature interval. Post weld heat treatment is in this
thesis the definition of a process performed after welding and with the objective of reducing
welding residual stresses.
dependent of the required strength and hardness of the material. A t higher cooling rates, more
pearlite is formed and the lamellae are finer and more closely spaced. Larger amount of pearlite
and fine lamellae gives higher strength and hardness. Observe that the cooling rate should not be
as high as for the quenching process where martensite is created.
It is common in the aerospace industry to use vacuum furnaces cooled with gas when performing
quenching and stress relief heat treating of components. In a gas cooled furnace is both the
heating- and the cooling sequence of the heat treatment operation performed in the charge volume.
Gas cooling has therefore an advantage in comparison with liquid cooled furnaces where the
component is quenched in a separate liquid bath. The charge volume is the volume in which the
component is positioned, see Figure 4a.
The gas pressure in kept low during the heating- and holding sequence of the heat treatment
operation in order to reduce oxidation on the surface o f the component. In the heat-treating furnace
in Figure 4 is the cooling gas inlets positioned in the top and bottom of the furnace. The top and
bottom holes are used both as inlets and outlets and this is done by revert the flow every 10
seconds. During one period of time is the top holes used as inlets and the bottom holes as outlets,
and by using a flap is the gas flow direction changed in order to use the bottom holes as inlets. The
heating of the component is mainly due to radiation from the walls of the furnace. These radiators
can be seen in Figure 4.
a) b)
Figure 4. Gas cooled vacuum furnace at Volvo Aero Corp. a) Charge volume with the
2. Material aspects in welding and heat treatment
simulations
A major concern when simulating welding and heat treatment is being able to model the varying
material behaviour. This is further complicated by temperature and rate effects. Also, the evolution
of microstructure during the various processes changes the material properties in response to the
thermo-mechanical history of the material. This can also cause transformation plasticity. The
microstructure, strain rate dependence and non-elastic behaviour are briefly described in the
following sections. Depending on the process studied, a model reflecting the material behaviour is
chosen. The simplest model giving an acceptable result is preferred to reduce material testing and
increase the computational efficiency. The material in all the cases presented in this thesis is a
martensitic stainless steel. The effect of the microstructure behaviour, strain rate and time on the
mechanical response is discussed in the following sections. The models compared in this thesis for
each process is described in Section 2.4 and 2.5.
2.1 Microstructure behaviour and thermal dilatation
The material consists initially of a ferritic and a pearlitic phase. The ferrite/pearlite mixture
changes to austenite when the temperature is increased above the A
3-temperature, which is
approximately 850°C. The phase changes can be illustrated by the thermal dilatation shown in
Figure 5. Point 1 represent the A
3temperature and Point 2, the start o f the martensite
transformation (M
s) due to rapid cooling. Thermal dilation is the sum of the thermal expansion and
the volume changes due to phase changes. The cooling rate in the dilatation test was 0.3°C/s and
represents the lowest cooling rate in the temperature interval between 800°C and 400°C during
welding. Most of the austenite phase transforms to martensite during the cooling sequence of
welding due to the high cooling rate. The simulation of austenite transformation has been done
using two different approaches. In the simplified transformation model (ST-model), only the peak
temperature controls the amount of austenite. A peak temperature higher then the A j-temperature
generated a fully martensitic structure. The phase composition remains unchanged i f the peak
temperature is less then A j . The austenite transformation is diffusion controlled and thereby
dependent on the temperature and time. The nucleation and growth process has been studied by for
example Johnson and Mehl [3], Avrami [4] and Kirkaldy et al. [5].
Figure 5. Thermal dilatation, e'
hvs. temperature
In the second transformatiotion model used in this thesis, the calculation o f austenite
transformation for an arbitrary thermal history is based on the theory presented by Kirkaldy et al.
[5]. The rate of transformation is described in Eq. 2.1, according to the expression proposed by
Oddy et al. [6] for low carbon steel. The model will be referred to as the extended microstructure
model (ET-model).
z
a(t) = n
V
n-1 >(
rt(
J zeu(
T)-
za
T(T)
(2.1)
-eu(T)-Z
a(t)
jThe parameter z
ais the austenite transformation rate, z„ is the volume fraction of austenite, z
euthe
equilibrium phase composition, and / the time. The material is fully austenised when z
ais equal to
one. The material consists of a mixture of ferrite and pearlite at the beginning of the simulation
(z
a=0). The parameter r i n Eq. 2.1 is temperature dependent. Oddy et al. [6] used the following
expression Eq. 2.2 for low carbon steel where T
0, r
e, and n are material constants.
r = T
n(T-A
elr-
(2.2)
The parameters used in Eq. 2.2 can be estimated from dilatometric tests. In this case, the
equilibrium phase composition z
euvaries linearly between the A
rand ^-temperature. The
transformation rate equation is integrated explicitly and time step splitting is used i f the
temperature increment is too large. Austenite transformation only occurs during heating associated
with the weld operation and the fraction does not decrease until the material transforms to
martensite.
The calculation of martensite fraction is based on Koistinen-Marburger's equation and is
dependent on the maximum austenite fraction z™
a xcreated during heating, Eq. 2.3. The
martensite transformation occurs. The latter term is often referred to as the transformation induced
plasticity strain (TRIP) and will be further discussed in the next section.
(i -b'-(M-T)) max i \
zm
=V~
e FZa (2-3)The major advantage of using the extended microstructure model is the smooth transition of the
martensite content in the heat-affected zone during welding. The phase content is used together
with a linear mixture of rule when calculating both the thermal dilatation and the mechanical
properties from the properties of the individual phases.
2.2 Transformation Induced Plasticity (TRIP)
The phase transformations do not only change the material's mechanical properties but also result
in volumetric and deviatoric transformation strains. Deviatoric transformation strains (TRIP) can
be orientated i f an applied stress is present during the phase transformation because the volume
differences between two phases generate microscopic internal stresses. At sufficiently high
stresses, plasticity is induced in the weaker phase; this is often referred to as the
Greenwood-Johnson mechanism, Leblond [7]. Any selective orientation (anisotropic orientation) in the created
martensite due to an external load is ignored, an assumption also used by Vincent et al. [8]. This
mechanism often referred to as the Magee mechanism. From experiments, it is known that
strain evolves in the direction o f the deviatoric stress Sy, Leblond [7]. The expression for
TRIP-strain rate according to Leblond [7] is;
q - l r - f r . . , ) . « ® . * . . , ,2.4)
Desalos [9] used an experimentally developed expression for 0(z);
<t>{z) = z{l-z) (2.5)
Equation 4 also includes a parameter K', an analytical expression for which has been proposed by
Leblond;
* • - - ! - £ (2.6)
Where AV/V (3 -é
m) is the change of volume during austenite to martensite transformation and
Oyfpa is the yield limit of the austenite phase. According to Leblond, typical values for K' are
between 50-10"
6and 100-10"
6MPa"
1. The function h in Eq. 2.4 describes the proportionality
between the applied von Mises stress and the transformation strain, it is given in Eq. 2.7.
1 "
+>cf<0.5-a
y("
+]T,e
p+Å£
p,z)
"
+lä>0.5-a
y(
n+lT,e
p+Åe
p,z)
h{a,a..) = \
1 + 3.5
"
+ 1c f 1^
c7
y[
n+xT,e
p+Ae
p,z) 2
In order to obtain an unconditionally stable algorithm, the transformation induced plasticity term
is evaluated implicitly. The deviatoric stress, s
ihand the function h are therefore evaluated at the
end of each time step. The transformation rate z is calculated in the middle of the increment but
the amount of the new phase z is calculated in the end of the time step.
The effect of TRIP is illustrated for an axial loaded rod in Figure 6. The compressive stress a has
been applied before the M
s-temperature and the specimen is cooled with a rate of approximately
10 °C/s. The change of diameter d is registered, the combined transformation strain e
t r aand
TRIP-strain d
prepresents the y-axis in Figure 6. An increased compression stress during the martensite
transformation generates an increased change in strain.
0,02 -i
Temp [°C]
Figure 6. Different applied compression stresses on a rod-specimen during martensitic
transformation.
2.3 Rate dependent plasticity and creep
In this section, the rate dependency and creep effects of the material are discussed. Plasticity and
creep are both non-elastic phenomena but are associated with different material mechanisms.
Strain-rate dependence is the expression of materials sensitivity to the strain rate. The elastic
properties are assumed to be rate-independent whereas the plastic deformation is rate dependent.
Strain rate dependence for metals results from the balance between strain hardening and dynamic
recovery. Dynamic recovery is the creation of low-energy dislocation structures (sub-grains)
during deformation. The rate of sub-grain development increases with temperature because of the
increase in mobility of vacancies and dislocations [10]. The strain rate dependence of a martensitic
stainless steel at 700 °C is illustrated in a strain rate jump test shown in Figure 7a). The strain rate
varies at three different levels e
2, £
3and , where £
3represents the highest strain rate.
Figure 7. a) Stress response during a tensile test at 700 °C with varying strain rates b) Strain rate
at different stress levels during a creep test at 700 °C.
A higher strain rate increases the resistance to plastic deformation and the stress in a tensile test
increases with an increasing strain rate. The plastic strain rate ejf can be described by a power law
Eq. 2.8 [11], where N and K are temperature dependent material parameters. In Eq. 2.8, a ,
o
vrepresent the equivalent stress and the yield limit, respectively. The driving force for an
increased plastic strain rate is the difference between the stress state and the yield limit.
£
P( ö - O >
;V
(2.8)
K
The evolution equation for isotropic hardening is shown in Eq. 2.9. The yield limit is assumed to
be dependent on the temperature T, accumulated equivalent plastic strain e
pand the phase
composition z.
cr
v(T, £
p, z) = a
v 0(T, z) + g , ( r , z)F
P+ Q
2{T, z)(l - ) (2,9)
The effect of including the strain rate dependence when simulating the welding process w i l l be
discussed in Section 2.4.
Creep is different from plasticity in the sense that the deformation is controlled by the diffusion of
atoms and vacancies, this is not the case for plasticity. The major driving force for creep is
temperature but the deformation is also influenced by the presence of stress [10]. The stress
dependence is shown in Figure 7b). Two different creep models have been used and compared in
this thesis, Norton's creep law [11] and a model referred to as the interpolation creep model.
Norton's law is a special case of Eq. 2.8 where the yield limit is set to zero. The creep strain rate in
the second model is dependent on the stress, temperature and the accumulated inelastic strain and
is not based on a specific equation, but on tabulated values. The creep rate is linearly interpolated
between two values tabulated for different temperatures, plastic strains and stresses. Uniaxel tests
are performed at three different stress levels at a number of temperatures. In Figure 7b), the strain
rate response is shown at three different stress levels at 700°C. The effect of the described models
2.4 Material model in welding and quenching analysis
The conditions during welding and quenching are similar in the respect o f temperature history and
load. The load rate (temperature increase) is higher during welding then during quenching where
the temperature is increased slowly up to the austenite temperature. The cooling rate from the high
temperature area can in some cases be higher during quenching then during welding. A welded
material is exposed to high temperature only for a short time and the creep effect is often ignored
[12]. The material effects and models used in welding analysis are described in this section.
An additive decomposition of the strain rate is used for all material models, Eq. 2.10. The total
strain rate is divided into elastic-, thermal-, plastic-, transformation- and TRIP strain rate
respectively.
£
<°< = e
e+ e
,h+e
p+ é"'
a+ £
,p(2.10)
The plastic strain rate can be rate independent or rate dependent and the effect of including
different phenomena is illustrated in a Satoh-test. The test is performed by, heating and subsequent
cooling a specimen uniformly without allowing any movement of the specimen's ends in the axial
direction. The force response at one of the ends is registered and the average stress can be
calculated i f the diameter ofthe specimen is known.
X
F,£
T[°C]
-RI-model 000 1200 1400 .t[s]
b)
Figure 8. a) Stress response during a modified Satoh-test. b) Temperature and strain rate history.
The stress response verses temperature in a modified Satoh-test is shown in Figure 8. The heating
rate was in this case 50°C/s and the cooling rate 20°C/s. The experiment is performed in a Gleeble
machine and the testing procedure is modified to obtain a stable force response. The Satoh-test is
modified in the sense that the axial strain e is controlled and given a negative value during the
heating sequence (compression) and a positive value during cooling.
In the simulations, three different material models have been compared. The Rl-model is a model
with Rate Independent plasticity, the RIT-model is the Rl-model plus transformation induced
plasticity and the RDT-model is based on Rate Dependent plasticity including
transformation-induced plasticity. Microstructure calculation is performed for all models. During the heating
sequence, all of the models show similar response but the maximum compression stress is
significant higher in the RDT-model. The largest difference between the models is observed
during cooling when martensite is created. The Rl-model does not capture the stress response
during the transformation but both the RIT- and RDT model is showing a similar behaviour as the
experiment.
2.5 Material model during stress relief heat treatment
The material is exposed to a temperature slightly below the austenite start temperature during
stress relief heat treatment. The material recovers during the process but no phase transformation
occurs. The heat treatment cycle can be divided into three sequences, heating, hold and the cooling
sequence, Figure 9. Three different combinations of material models are compared in the heat
treatment analysis and the acronyms C l , C2 and C3 are used. The models effect on the global
deformation is investigated in this section.
Holding
temperature
C I , 3-model
Temperature
•
•
- No creep active
- Creep active
C2-model
Temperature
Time
Heating Holding Cooling
sequence sequence sequence
Heating Holding Cooling
sequence sequence sequence
Figure 9. Different procedures for applying the interpolation creep model.
In all cases, a creep model is used in combination with rate independent plasticity, see Eq. 2.11
where e
eis elastic strain-, é '
Ai s thennal-, £
pplastic- and e
ais the creep strain rate. A n additive
decomposition of these strain rates is assumed.
£
m= £
e+ £
, h+ £
P+ £
C r(2.11)
This constitutive relation has earlier been used by Josefson [13] and the independent assumption
between the plastic- and creep strain increment is shown by Otterberg [14] for a 21/4 C r l M o steel.
He showed in his study that that the parameters in the creep law are almost independent o f the
magnitude of the applied plastic strain. The time dependent plasticity (creep), is simulated by the
use of Norton's law [10] and by using the interpolation model described in Section 2.3.
In model C1, the interpolation creep model is activated only during the holding sequence of the
heat treatment cycle, Figure 9 and no creep strain is generated during the heating and cooling
sequence. The only difference between model C I and C3 is that Norton's law replaces the
interpolation creep model. The interpolation creep model is active in all sequences when the
C2-C I - and C2-C3-model during the holding sequence. In Figure 10 is a part of a aerospace component
shown and the change of the axial distance a between the top side of the bearing house and the
flange is studied.
Time [s]
Figure 10. Change in distance a during the stress relief heat treatment using different ways to
apply the creep.
In Figure 10 is the change in a during the heat treatment process shown. Observe that the initial
value of the result parameter a is negative due to the distortion during welding. The result shows
only minor differences in residual deformation when different creep models are used.
3. Simulation of welding
The finite element method has been used since early 1970's in order to predict stresses and
deformations as a result of welding [15-17]. The method has become more commonly used in the
aerospace during the last decade. For example Roberts et al. [18] used welding simulations to
develop a process model for electron beam welding that predict residual stresses and distortion on
compressor assemblies. Simulations of large fabricated components have earlier been done by for
example Rick et al. [19] and Andersen [20]. Large simulation models are computational
demanding and often require long modelling time. This is a problem when performing
manufacturing simulations in the early stage of the product development. Andersen used a
local/global approach where simulations results on a detailed solid model were mapped on a global
shell model. Simplified models may be used to keep the modelling time short when making
preliminary preparation in the manufacturing planning. These models must describe the
deformation behaviour qualitatively correct so that it can be used to indicate whether changes in
the manufacturing are an improvement or not. In the following chapters are different simulation
models discussed, and methods for simulating the heat input and filler material during welding are
shown.
3.1 Simulation models in finite element analysis
Simulations are based on choice of finite element formulation and a corresponding finite element
model. Modelling the welding process includes the representation of thermal- and mechanical
loads, the material behaviour and the choice of geometric model. The type of finite element
formulation and geometric model for welding simulation is discussed in this section. The choice of
geometric model depends on the geometry of the component, the nature of the boundary
conditions and the desirable accuracy of the result. Lindgren [21] has categorised and named the
different accuracy levels. They depend on the scope of the analysis to be performed. A simulation
where the transient strains and stresses are wanted is called an accurate simulation, according to
his definitions.
a) b) c)
Figure 11. Geometrical models in welding analysis, a) 2D-plane strain model, b) 3D-shell model,
c) 3D-solid model.
Geometrical models are shown in Figure 11, a is a plane strain model where the heat source is
moving through the plane, b is a 3D-shell model where the stresses in the thickness direction is
neglected and c is a model with solid elements. The different geometrical models give different
transient deformation behaviour. It is of great importance not only to choose accuracy level but
also to decide what type of deformation mode to be studied as they determine the choice of
geometric model to a subset of the general 3D-solid model. The different deformation modes are
exemplified in Figure 12.
2 )
4
3.2 Heat input model
There are different methods to introduce the thermal load in a welding analysis. One way is to
prescribe the temperature in certain volume of material and adjust the temperature level in order to
obtain an acceptable dimension of the fusion zone (FZ). A more sophisticated method is to use a
double ellipsoid heat source first recommended by Goldak [22] et al. The heat flux is in this case
distributed as a double ellipsoid Different welding processes can be simulated by adjusting a
limited number of parameters.
The double ellipsoid heat source is used for all geometrical models. In the 2D-model, the heat
source is passing through the cross section, as illustrated in Figure 11a. When using a shell model
is the heat input on the top and bottom of the shell. The volumetric heat source is replaced by a
surface heat source and the fraction of energy applied on the top- and bottom side is obtained by
integrating the volumetric heat source and lump the energy on the shell's surface.
3.3 Joining of material and treatment offiller material
Welding can be done with or without filler material depending on the process and requirements
on the weld geometry. Filler material is commonly used in GTA- and laser welding. The
modelling of addition of filler material poses some extra complications in simulation of welding.
Lindgren et al. [23] have compared two different approaches, the quiet element- and the inactive
element technique when performing multipass welding simulations. In the quiet element technique
is the filler material already included in the model in the beginning of the analysis but the
corresponding elements are given low conductivity and stiffness so they do not affect the rest of
the model. The elements corresponding to the filler material are not included at all in the model
until the weld is laid, when using the inactive element approach. Lindgren et al. [23] showed that
both techniques can give the same result but the computational effort was reduced and the
condition number of the stiffness matrix was improved by using the inactive element technique.
In this thesis, only single pass welds are considered and the inactive element technique is used
when modelling the joining of material. One row of elements is deactivated at the start of the
analysis to simulate the gap between the welded plates. The volume of the inactivated element
corresponds to the amount of filler material added during the welding sequence. These inactivated
elements do not contribute to the stiffness matrix but they are active in the thermal part of the
calculation. In Paper I , the elements are activated when the centre of the heat source is one heat
source length from the element edge. This method has been improved to reduce the influence of
the molten material on the global deformation. In Paper I I I , the elements are activated when the
temperature in the beginning of the increment is larger then the melting temperature and when the
temperature increment is less then 0.
The molten material is treated as a soft solid The stiffness or yield limit of the material can only
be decreased to a certain level until numerical problems occurs in the solution procedure. The
value of the lowest yield limit does affect the deformation result. One example is the gap
behaviour when no tack-welds are present. The deformation behaviour o f a point during
GTA-welding is shown in Figure 13 with different minimum yield limit. The measured result is
significant lower then the calculated.
Time [s]
a) b)