from massalski to micress and beyond: an introduction to
TRANSCRIPT
From Massalski to MICRESS and beyond: An introduction to
MICRESS and current trends in Integrated Computational
Materials Engineering “ICME”
Dr. rer.nat. Georg J. Schmitz
Version August 2014
First Edition 1986
ca. 1980: first PCs
8086- Processors
about 1960
about 1980:
first networks / Internet
1973: my first calculator (DM 300,--) …150 €
thermodynamic databases are NOT (!!) just
collections of experimental data in an Excel sheet !!
Thermodynamic databases are based on physical models allowing
extrapolations into „unknown areas“
0
10
20
30
40
1 2 3 4 5 6 7
y
x
parabolaexample:
y-y0 = a(x-x0)2
here: y0=1 a=1 x0=0
xs
m
ideal
mmm GGGG 0
i
i
SER
mm TdTcTbTaHG )ln(
o
BB
o
AAm GxGxG 0
BBAA
ideal
m xxxxRTG lnln
0
, )(k
k
BABA
k
BA
xs
m xxLxxG
....)()( 2
,
2
,
1
,
0
BABABABABABA xxLxxLLxx
The CALPHAD method
CALculation of PHAse Diagrams
Models for the thermodynamic properties
of each phase G(T, P, y)
Database for model parameters
Predictive calculation of:
thermodynamic properties
equilibrium states
phase diagrams
Fundamental
theories
Empirical
rulesExperimental
Information
www.calphad.org
1969 Formation of CALPHAD.
1971 Sub-lattice model for 2
comp. (Hillert and
Steffansson, KTH).
1977 Development of
Thermo-Calc starts
Database for Model
Parameters
•
•
•
•
•
•
•
•
•
•
•
•
Tsol~ 1240 °C
Tliq ~ 1410°C
Fe-4Cr-8Mo-2V-0.3Mn-0.3Si-1C
The CALPHAD method
CALculation of PHAse Diagrams
Models for the thermodynamic properties
of each phase G(T, P, y)
Database for model parameters
Predictive calculation of:
thermodynamic properties
equilibrium states
phase diagrams
Fundamental
theories
Empirical
rulesExperimental
Information
www.calphad.org
1969 Formation of CALPHAD.
1971 Sub-lattice model for 2 comp.
(Hillert and Steffansson, KTH).
1977 Development of Thermo-Calc
starts
2007
1986
possible
Not available
Determination of phase fractions
Prediction of onset of precipitate formation
Determination of temperatures for phase transitions
Estimation of solidification behaviour
Determination of thermodynamic data
Information on kinetics
Information on microstructure
Information about materials properties
Al
Mo
Cr
),,(ln PTxfRTMB
Diffusion without a chemical gradient:
- Tracer diffusion coefficients
Diffusion under a chemical gradient:
- Chemical interdiffusion coefficients
- Intrinsic diffusion coefficients
Logarithm of the Atomic Mobility for
Individual Elements
Applications
~
D
0
0.02
0.04
0.06
0.08
0.1
0.12
-1000 -500 0 500 1000
Ma
ss F
ract
ion
Distance (m)
Cr
Co
W
Ta
Al
Ti
Mo
Re
HfNb
René-N4 René-N5
g g
6.35 mm 6.35 mm
Double geometric grid: 200 points
Experimental work performed by T. Hansen, P. Merewether, B.
Mueller, Howmet Corporation, Whitehall, MI.
From: C. E. Campbell, Metallurgy Division, NIST
D is a 10×10 matrix where all coefficients
depend on concentration
René-N4/René-N5 at 1293 °C for 100 h
Databases used
Thermodynamics: ThermoTech
Kinetics: NIST Ni-mob
possible
still not available
Determination of phase fractions
Prediction of onset of precipitate formation
Determination of temperatures for phase transitions
Estimation of solidification behaviour
Determination of thermodynamic data
Information on kinetics (diffusion)
Information on microstructure
Information about materials properties
www.micress.de
van der Waals (1893)
Korteweg (1901)
Landau-Ginzburg (1950)
Cahn-Hilliard (1958)
Halperin, Hohenberg & Ma (1977)
Langer (1978) phase field
Fix, Caginalp (1986) phase field
Kobayashi (1992) dendrites with phase field
Steinbach (1996) multi-phase-field-model
Elder (2002) phase-field crystal models
2010 Physica D 94 (1996)135
t,x
The phase-field equation(s) .....an own area of research
ss2
ssss
2
s 11211
t,x
G
Stabilise
- +
Move Smooth
t,x
~t,x
~T t,x
~c t,x
cT ,dG
t,x
t,x
200 µm
r = 3 µm
4cos(0 1
Stabilise
- +
Move Smooth
ss2
ssss
2
s 11211
t,x
G
4cos(0 1
cited > 300 times (status Feb 2014)
one phase field for each phase: L+ + g= 1
Basic ideas: (see I.Steinbach et al. Physica D 94 (1996) 135)
definition of one phase field for each phase AND for each grain of a phase
pairwise interaction for each pair of phases/grains like in standard phase-field
possibility of implementation of specific phase/grain boundary properties
Specific aspects:
1D-simulation unable to reproduce multi-
phase interactions
physics of triple junctions
Further concepts:
coupling to thermodynamic databases
coupling to mobility databases
mobility
database
Use of Thermodynamic Data in MICRESS®
multicomponent diffusion solver
M I C R E S S ®
nucleation model
temperature solver
multiphase-field solver
time loop
Thermo-Calc
CALPHAD database )GwK()t,x(
?TT c ritu n d
cD)t,x(c
g
possible
still not available
Determination of phase fractions
Prediction of onset of precipitate formation
Determination of temperatures for phase transitions
Estimation of solidification behaviour
Determination of thermodynamic data
Information on kinetics
Information on microstructure
Information about materials properties
Information about properties of component
Cluster of Excellence
Integrative Production Technologies for
High Wage Countries
Virtual Process Chains for Processing of
Materials
Speakers:
Dr.-Ing. Ulrich Prahl
Dr. rer.nat. Georg J. Schmitz
Seite 42 © RWTH Aachen University staff involved (2013):
about 30 scientists (8 scientists full time equivalent)
Virtual Process Chains for Processing of Materials
Scopes
integrative virtual description of processes and microstructure evolution along the production chain
prediction of effective materials properties from calculated microstructures
interfacing between microstructure simulations and macroscopic process simulations
virtual documentation of the product history towards life cycle modelling
verification for different test-cases of scientific and economic interest
- casting - solidification - hot forming - cold forming - heat treatment - joining - coating -
Seite 43 © RWTH Aachen University
Example of a process chain
co
mp
on
en
t m
ikro
s
ub
-µ
rolling forging carburizing welding cooling
Integration along process chain
heating
averaged
properties
boundary
conditions
precipitates
Grain growth
Seite 44 © RWTH Aachen University
Numerical tensile tests
200
400
600
800
1000
1200
1400
0,00 0,02 0,04 0,06 0,08 0,10 0,12 0,14 0,16 0,18 0,20
true strain
tru
e s
tre
ss (
MP
a)
20%
+5%
-5%
Amount of martensite: 20% +/-5
Annealing temperature: 740°C
FE Simulation
Experiments
Numerical tensile tests of a simulated
microstructure (DP600 steel) by means
of RVE-FE and experimental bulge test
show good agreement
PHD Thesis
C. Thomser IEHK RWTH Aachen (2009)
Seite 45 © RWTH Aachen University
Crack propagation in virtual microstructure
Seite 46 © RWTH Aachen University
Effective properties
RVE: pearlite in ferrite matrix
U-O-forming simulation of
a pipeline tube
equivalent plastic
microstrain
localization in critical
regions:
applying local macrostrains
on the RVE
virtual test/
homogenization
effective anisotropic
flow curves
Ferrite-Cementite
bilamella
Seite 47 © RWTH Aachen University
…Integrated Computational Materials Engineering „ICME“….
appeared in April 2012
ISBN-10: 3-527-33081-X
ISBN: 978-3-527-33081-2
to appear in Chinese language
edition in August 2016
page 48
www.icmeg.eu
The Integrated Computational Materials Engineering expert group
- EU project ICMEg -
www.icmeg.eu
www.icmeg.info
consortium: 11 partners, 6 countries vision: plug&play in ICME
approach: global, open standards How to do in practice? Read more:
Possible/in reach
still not available
Determination of phase fractions
Prediction of onset of precipitate formation
Determination of temperatures for phase transitions
Estimation of solidification behaviour
Determination of thermodynamic data
Information on kinetics
Information on microstructure
Information about materials properties
Information about properties of component
Life cycle modelling
Inverse modelling
Adv.Eng.Materials
2006
Adv.Eng.Materials
2009
Int. J. Mater Res.
2010
Adv.Eng.Materials
2003
Thank you very much for your attention!
www.micress.de www.thermocalc.de
www.thermocalc.se