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Strengthening Mechanisms and Their Relative
Contributions to the Yield Strength of Microalloyed Steels
Junfang Lu 1, Oladipo Omotoso 2,
J. Barry Wiskel 3, Douglas G. Ivey 3 & Hani Henein 3
1 Enbridge Pipelines Inc., Edmonton, Alberta
2 Suncor Energy Centre, Calgary, Alberta
3 Dept. Chemical/Materials Engineering, University of Alberta, Edmonton, Alberta
July 10, 2013
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University of Alberta Facts
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• 80% undergraduate students
• 20% graduate students
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• $0.46M Cdn Research
Outline
I. Introduction
II. Objectives
III. Experimental Methods
IV. Tests and Results
Grain size measurement
Precipitate size, morphology and chemistry
ICP analysis of the supernatant
Rietveld refinement of XRD data
Effect of microalloying content, CT/ICT on the amount of nano-sized
precipitates
Strengthening contributions
V. Conclusions
VI. Acknowledgements
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Thermomechanical controlled processing - to control microstructure evolution Te
mp
era
ture
, º
C
Time
1400
1000
800
600
400
200
Accelerated
Cooling
Recrystallized Austenite
Tnr
Pancaked Austenite
Ar3
PF P
BF (or AF)
Ms
PF – Polygonal Ferrite
P – Pearlite
BF – Bainitic Ferrite
AF – Acicular Ferrite
Finish Rolling
Reheating
Rough Rolling
Coiling
A schematic CCT diagram for microalloyed linepipe steels (Ref: D. Qi, Patent)
Grain size effect
Solid solution strengthening
Precipitation strengthening
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Objectives
To understand the strengthening mechanisms of microalloyed steels
I. To determine strengthening contribution due to grain size effect
II. To determine strengthening contribution due to precipitation effect
To characterize precipitate size, morphology and chemistry
To quantify the amount of nano-sized precipitates
To understand the nano-sized precipitation as a function of steel
chemistry and processing histories
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Challenges associated with precipitate characterization
Fine sizes of precipitates
Wide particle size distribution
Low volume fraction
Precipitates have same crystal structure (NaCl-type), with
similar lattice parameters
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FRT* = normalized finish rolling temperature to that of X80-B4F steel
CT/ICT* = normalized coiling/interrupted cooling temperature to that of X80-B4F steel
** = intended values
For Grade 100 and X100 steels, steels were deformed by leveling or rolling at ICT temperature
X100 steels are experimental, pilot scale steels
Chemical compositions & processing histories
Steel C
(wt%)
N
(wt%)
Si
(wt%)
Nb
(wt%)
Ti
(wt%)
Mo
(wt%)
V
(wt%)
FRT* CT/ICT* CR
(ºC/s)
X70-564 0.0398 0.0118 0.23 0.069 0.023 0.2 0.001 0.94 1.04 15**
X80-A4B 0.035 0.0058 0.283 0.094 0.017 0.305 0.003 1.05 0.93 15**
X80-B4F 0.052 0.0061 0.128 0.077 0.009 0.299 0.002 1.00 1.00 15**
X80-462 0.03 0.0098 0.27 0.091 0.013 0.297 0.002 0.94 1.04 15**
X80-A4F 0.052 0.0055 0.115 0.044 0.009 0.404 0.003 1.00 0.90 15**
Grade 100 0.08 0.011 0.244 0.094 0.06 0.301 0.047 1.07 1.09 15**
X100-2A 0.039 0.005 0.11 0.037 0.013 0.41 0.003 1.00** 0.71 35
X100-2B 0.065 0.0059 0.22 0.047 0.009 0.4 0.07 1.00** 0.64 34
X100-3C 0.064 0.0063 0.33 0.05 0.009 0.4 0.003 1.00** 0.80 19.1
Steel chemistry and normalized FRT and CT/ICT
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Experimental methods – combination of different techniques
Carbon replicas
SEM/TEM
Size;
morphology;
chemistry
Steel Dissolve sample in solution
Centrifuge, remove portion of liquid
Centrifuge again
Dilute solution
Residues ICP analysis
SEM/TEM XRD
Mass balance
Solution
Relative amounts of crystallographic phases
Rietveld refinement
Steel
SEM
Grain size
Precipitate
Matrix dissolution Carbon replicas
Steel
TEM
Precipitate
distribution
in matrix
Thin foils Steel
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X70-564 X80- 462
Grade 100 X100- 3C 9/29
Hall-Petch equation
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Grade 100 – thin foil
{111}
{200}
{220}
BF-TEM DF-TEM
11/29
Grade 100 – carbon replica
{200}
{111} {220}
Grade 100
0
100
200
300
0 2 4 6 8 10 12 14 16 18 20
Energy (keV)
Inte
nsi
ty
C
O
Cu
Nb
Ti
Fe
Cu
Cu Nb
Nb Mo
Mo
Ti V
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Grade 100 – matrix dissolution
{111}
{200}
{220}
Matrix dissolution using HCl Matrix dissolution using 10% AA
(10% acetylacetone + 1% TMAC
(tetramethylammonium chloride) + methanol)
Nb/Mo- rich
0
50
100
150
200
250
300
350
0 2 4 6 8 10 12 14 16 18 20
Energy (keV)
Inte
nsi
ty
Si
Nb
Ti
Fe
Cu
Cu
Nb
Nb
Kb1
Ca
Mo
Mo Fe V
Ti
Mo
13/29
X100-3C – carbon replica
100 nm
20 nm 14/29
Wt% of Nb - based on steel chemistry and ICP analysis
0.00
0.02
0.04
0.06
0.08
0.10
0.12
X70-564 X80-462 X80-A4B X80-B4F X80-A4F Grade100 X100-2A X100-2B X100-3C
wt%
of
Nb
Steel
Nb amount in solid solution
Nb amount in precipitate
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Wt% of Mo - based on steel chemistry and ICP analysis
0.00
0.10
0.20
0.30
0.40
0.50
X70-564 X80-462 X80-A4B X80-B4F X80-A4F Grade100 X100-2A X100-2B X100-3C
wt%
of
Mo
Steel
Mo amount in solid solution
Mo amount in precipitate
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• Ti, Nb and V carbides, nitrides or carbonitrides have NaCl-type, fcc structure
• Lattice parameters are similar, making it difficult to identify specific precipitates
XRD analysis of residues (preliminary analysis)
0
2000
4000
6000
8000
20 40 60 80 100 120
2θ
Inte
nsit
y (
Co
un
ts)
Grade 100
X70-564
X80-462
X80-B4F
NbC-rich
TiN-rich
(111)
(111)
(200)
(200) (220)
(220) (311)
(311) (400)
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yi: observed (and calculated) intensities at each step
wi: weighting factor for each observation
wa: relative weight fraction of phase a in a mixture of j phases
SF: refined scale factor, which is proportional to the number of unit cells of phase a in the specimen
M: mass of the molecular formula
Z: number of formula units per unit cell
V: volume of the unit cell
Rietveld refinement: Least squares profile fitting (minimization procedure)
To minimise a function S which represents the difference between y(calc) and y(obs)
Full pattern profile refinement
Simultaneous crystal structure refinement
Quantitative phase analysis
Rietveld refinement of XRD pattern
MinimumcalcyobsywS ii
i
i 2))()((
j
jj
aaa
MZVSF
MZVSFw
)(
)(
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908580757065605550454035
9,000
8,000
7,000
6,000
5,000
4,000
3,000
2,000
1,000
0
-1,000
908580757065605550454035
9,000
8,000
7,000
6,000
5,000
4,000
3,000
2,000
1,000
0
-1,000
Overall XRD pattern profile fitting
Rietveld refinement of XRD data (Grade 100)
908580757065605550454035
9,000
8,000
7,000
6,000
5,000
4,000
3,000
2,000
1,000
0
-1,000
-2,000
908580757065605550454035
9,000
8,000
7,000
6,000
5,000
4,000
3,000
2,000
1,000
0
-1,000
-2,000
Ti0.9Nb0.1N
908580757065605550454035
9,000
8,000
7,000
6,000
5,000
4,000
3,000
2,000
1,000
0
-1,000
-2,000
908580757065605550454035
9,000
8,000
7,000
6,000
5,000
4,000
3,000
2,000
1,000
0
-1,000
-2,000
908580757065605550454035
9,000
8,000
7,000
6,000
5,000
4,000
3,000
2,000
1,000
0
-1,000
-2,000
908580757065605550454035
9,000
8,000
7,000
6,000
5,000
4,000
3,000
2,000
1,000
0
-1,000
-2,000
Ti0.5Nb0.5C0.5N0.5
Nb0.7Ti0.3C0.5N0.5
908580757065605550454035
9,000
8,000
7,000
6,000
5,000
4,000
3,000
2,000
1,000
0
-1,000
-2,000
908580757065605550454035
9,000
8,000
7,000
6,000
5,000
4,000
3,000
2,000
1,000
0
-1,000
-2,000
Nb0.48Mo0.28Ti0.21V0.03C
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Precipitate information
Steel Precipitate chemistry Precipitate size (nm)
X70-564
Nb0.52Ti0.43Mo0.05C0.5N0.5
Nb0.79Ti0.15Mo0.06C0.5N0.5
Nb0.58Mo0.42C
20-40
20-40
5
X80-A4B
Ti0.52Ti0.48C0.5N0.5
Nb0.9Ti0.1C0.5N0.5
Nb0.68Mo0.32C
60-80
25-70
5
X80-B4F
Ti0.72Nb0.28N
Nb0.57Ti0.43C0.5N0.5
Nb0.92Ti0.08C0.5N0.5
Nb0.78Mo0.22C
80-100
85-135
40-100
4.5
X80-A4F
Ti0.76Nb0.24N
Ti0.51Nb0.49C0.5N0.5
Nb0.86Ti0.14C0.5N0.5
Nb0.74Mo0.26C
100-200
20-30
20-30
4
X80-462
Ti0.76Nb0.24N
Ti0.55Nb0.45C0.5N0.5
Nb0.86Ti0.14C0.5N0.5
Nb0.8Mo0.2C
100-200
80-100
40-90
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Precipitate size and chemistry
Phases NbN NbC TiN TiC MoC VN VC
Lattice
parameter (nm)
0.43927
0.44698
0.42417
0.43274
0.428
0.41392
0.41820
Steel Precipitate chemistry Precipitate size (nm)
Grade 100
Ti0.9Nb0.1N
Ti0.77Nb0.23C0.5N0.5
Ti0.5Nb0.5C0.5N0.5
Nb0.7Ti0.3C0.5N0.5
Nb0.48Mo0.28Ti0.21V0.03C
500-3000
100-500
100-200
100-200
4.5
X100-2A Ti0.70Nb0.26Mo0.04C0.5N0.5
Ti0.54Nb0.41Mo0.05C0.5N0.5
30
20
X100-2B
Ti0.66Nb0.29V0.05C0.5N0.5
Nb0.53Ti0.42V0.05C0.5N0.5
Nb0.85Ti0.13V0.02C
80
60
40
X100-3C Ti0.5Nb0.47Mo0.03C0.5N0.5
Nb0.67Ti0.3Mo0.03C0.5N0.5
40
20
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Effect of microalloying content on vol% of nano-precipitates
0.00%
0.05%
0.10%
0.15%
0.20%
0.03 0.04 0.05 0.06 0.07 0.08 0.09 0.1
Vo
l% o
f n
an
o-p
recip
itate
s i
n s
teel
wt% of Nb in steel
X80-B4F
X80-A4B
X80-462
Grade100
X70-564
X80-A4F
X100
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Effect of CT/ICT on vol% of nano-precipitates
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Superposition of strengthening mechanisms
2. Root mean square summation (Pythagorean superposition)
2222
pptssgbi
3. Combination of linear and root mean square summation
ssipptgb 22
Linear superposition can be assumed to be valid
Structural scales are very different: σi (scale of atomic distances) and σgb (micron scale)
Strengthening mechanisms are different: σss and σgb
Solute concentration is relatively low for microalloyed steels, does not change σppt mechanism
Strong synergism between grain boundary and particle hardening
1. Linear summation (overestimate σy because of synergy effect)
4
2/12/1
10*125.6ln
8.10)(
X
X
fCkdkMPa iiyipptssgbiy
24/29
Comparison with yield strength of steels
300
400
500
600
700
800
900
300 400 500 600 700 800 900
Str
en
gth
su
perp
osit
ion
(M
Pa)
Yield strength - experimental (MPa)
Experimental yield strength
Linear summation
Combination of root mean square and linear summation
Linear (Experimental yield strength)
X70
X80
X100-2B
X100-3C Grade100
X100-2A
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Individual strengthening component – combination of root
mean square and linear summation
0%
10%
20%
30%
40%
50%
60%
70%
80%
90%
100%
X70-564 X80-462 X80-A4B X80-B4F X80-A4F Grade100 X100-2A X100-2B X100-3C
Ind
ivid
ual
str
en
gth
en
ing
co
mp
on
en
t
Steel
σi Solid solution strengthening Precipitation strengthening Grain size strengthening26/29
Conclusions
I. Grain size decreased with increasing grades of steels; behaviour
followed Hall-Petch relationship – higher cooling rates and lower
CT/ICT promoted grain refinement
II. Matrix dissolution methods were effective in extracting sufficient
amounts of precipitates for quantitative analysis
III. Rietveld refinement of XRD data, combined with electron
microscopy, was successfully used to identify and determine
relative amounts of different precipitate phases
IV. X70, X80 and Grade 100 steels had similar processing histories -
higher microalloying content increased precipitation, leading to
higher volume fractions and number densities of nano-precipitates
27/29
Conclusions
V. For X100 steels, no nano-precipitates (≤5nm) were found - lack of
fine precipitates was due to the low ICT temperature
VI. Nb/Mo rich nano-precipitates (<5 nm) and solid solution
strengthening were quantified in X70, X80 and Grade 100 steels
and contributed significantly to the yield strength (about 40 to 50%)
VII. For all steels, grain refinement was a major contributor to
strengthening
28/29
Acknowledgements
EVRAZ Inc. NA
Natural Sciences and Engineering Research Council (NSERC) of Canada
Companhia Brasiliera de Metalurgia e Mineração (CBMM)
Beta Technology
Institute of Materials, Minerals and Mining (IOM3)
Naila Croft, Ben Micó and Geórgia Gomes Bemfica
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