Precipitation-Strengthened Al-Sc-Ti Alloys
Marsha van DalenDavid Dunand, David Seidman
Northwestern UniversityDept. of Materials Science and
EngineeringEvanston, IL
This study is supported by the US Department of Energy through grant DE-FG02-98ER45721.
Introduction: Al-Sc alloys Most current Al alloys are limited
to low temperature usage (<200ºC ) because of the dissolution and/or coarsening of their precipitates.1
Al-Sc alloys, however, form nanosize, coherent Al3Sc (L12 structure) precipitates which exhibit low coarsening rates at 300ºC-350ºC.
Significant improvement in creep resistance over pure Al.2
1Polmear IJ, Light Alloys: Metallurgy of the Light Metals, Edward Arnold 1981.2Marquis EA, Seidman DN, Dunand DC, Acta Mat. 50 (2002) 4021-4035.
L12 StructureAl atomsSc atoms
Al-Sc Phase Diagram
1Hyland, Met. Trans. A, 23A (1992) 1947-1955.2Drits M Ye., Ber LB, Bykov YG, Toropova LS, Anastas'eva GK, Phys. Met. Metall., 57 (6) (1984) 118-126.
-Al + Al3Sc
Sc has limited solid solubility in -Al.
Sc is most potent strengthener on a per atom basis.
More potent than Zn, Cu, Mg, Li and Si.2
Ternary alloying elements Ternary additions can alter the
properties of Al-Sc alloys. Mg for solid solution strengthening Zr partitions to Al3Sc phase
Diffusivity of Zr is over 4 orders of magnitude smaller than Sc1 at 300ºC which leads to a lower coarsening rate compared to the binary.
Reduces the lattice parameter mismatch2 between Al and Al3Sc which also leads to a lower coarsening rate.
Segregates to the -Al/Al3Sc heterophase interface.3
1Fujikawa SI, Defect and Diff. For. 143-147 (1997) 115-120.2Harada & Dunand, Mater. Sci. & Eng. A, 329-331 (2002) 686-695.3C.B. Fuller, J.L. Murray, D.N. Seidman, to be submitted for publication, 2005.
Al-Sc-Ti alloysTi as a ternary alloying element:
Low diffusion rate in Al Smaller than Zr by factor of ca. 20 at 300ºC1
High solubility in Al3Sc2
Replacing up to 50% of Sc atoms. Ti reduces the lattice parameter mismatch
between -Al and Al3(Sc,Ti) precipitates. Has the potential of reducing the
coarsening rate since the diffusion and elastic strain energy are reduced.
1Bergner D, Van Chi N, Wissens. Zeit. der Padag. Hochschule “N.K. Krupskaja” Halle XV (1977), Heft 3.2Harada & Dunand, Mater. Sci. & Eng. A, 329-331 (2002) 686-695.
Al-Sc-Ti Ternary Phase Diagram
Composition analyzed: Al-0.06at.%Sc-0.06at.%Ti
The composition is in the single phase -Al region during homogenization at 640ºC.
It is in the three phase region during aging at 300ºC and 350ºC.
No Al3Ti precipitates were observed.
J.L. Murray, ALCOA
350ºC 300ºC
Vickers Microhardness Sc is more effective
strengthener at room temperature than Ti.
Even the addition of 0.005 at.% Zr increases the hardness to several hundred MPa over the alloy with Ti additions.
E.A. Marquis, D.N. Seidman, D.C. Dunand, Acta Mater. 51 (2003) 4751-4760.E.A. Marquis, D.N. Seidman, Acta Mater. 49 (2001) 1909-1919.C.B. Fuller, PhD Thesis, Northwestern University, 2003
1 hr 1 day 1 week
Vickers Microhardness Significant hardening at
300ºC Overaging occurs after
16 days. Decrease in hardness
with increasing temperature due to coarsening of ppts.
No significant hardening above 320ºC
Due to heterogeneous nucleation at higher temperatures
Still significant hardening for samples aged at 300ºC first before aging at higher temperatures likely due to diffusion of Ti into the precipitates.
1 hr
1 day1 week
Triple Aged Sample: 300ºC/24 h - 400ºC/10 days - 450ºC/48 hDouble Aged Sample: 300ºC/24 h - 425ºC/48 h
Precipitate MorphologyDark Field TEM images showing changes in precipitate size, shape and distribution with aging treatment:
(a) 300C / 64 days [110] zone axis;
(b) 320C / 1 day. [100] zone axis;
(c) 330C / 1 day. [211] zone axis;
(d) 300C / 1 day, 400C / 10 days, 450C / 2 days, [110] zone axis.
Coherency of Al3Sc Precipitates
The Al3Sc precipitates remain coherent up to temperatures of 320ºC
The precipitates display Ashby-Brown strain contrast typical of coherent precipitates.
Consistent with binary alloys in which precipitates remained coherent up to 40 nm in diameter.1
BF TEM image of Al-0.06Sc-0.06Ti aged at 320ºC for 24 h.1E.A. Marquis, D.N. Seidman, Acta Mater. 49 (2001) 1909-1919.
Coarsening Models LSW Coarsening Theory predicts for binary alloys for steady-
state:1,2
Average precipitate radius, <R> t1/3
Precipitate Number Density t-1
Supersaturation t-1/3
For ternary alloys the time exponents are the same.3
Assumptions: Negligible volume fraction. No elastic interaction among ppts. Ppts. have spherical shape and are randomly distributed. Only takes into account diffusion - not coagulation or coalescence of precipitates. Composition of precipitates and matrix is in quasi-steady-state, i.e. dC/dt0 Off-diagonal terms of diffusion tensor neglected.
1Lifshitz IM, Slyozov VV, J Phys. Chem. Solids, 19 (1961) 35-50.2Wagner C, Z. Elektrochem, 65, (1961) 581-591.3Kuehmann CJ, Voorhees PW, Met. Mat. Trans. A, 27A (1996) 937-943.
1C.B. Fuller, PhD Thesis, Northwestern University, 2003
Alloy Composition (at.%) Time exponentsAl-0.06Sc-0.06Ti 0.1Al-0.06Sc-0.005Zr 0.04Al-0.09Sc-0.05Zr 0.05
Precipitate Size vs. Time at 300ºC
Average precipitate radius only increases slightly with time for aging at 300ºC.
Much smaller time exponent than predicted.
Similar trends observed for Al-Sc-Zr alloys.1
Indicates coarsening is occurring more slowly than predicted by coarsening models.
3-Dimensional Atom Probe (3DAP)
3DAP Microscopy Results
3D reconstruction showing Al3Sc precipitate in sample aged for 96 h. at 300ºC~125,000 atoms
• Sc atoms• Ti atomsAl atoms omitted for clarity.
3DAP Microscopy Results:Ti Concentration vs. Time
Ti concentration in Al3Sc precipitates increases with time at 300ºC.
Only small amount incorporated into the ppts. since the diffusion of Ti in Al is slow.
Apparent interfacial segregation at longer aging times.
Similar to results obtained for Al-Sc-Zr alloys.
Based on 9 at.% Sc isosurface.
Proximity Histogram of Ti for various aging times
precipitate
matrix
3DAP Microscopy Results:Concentration vs. Time
Sc concentration in precipitate phase decreases over time.
Sc atoms replaced by Ti atoms.
System thus not in equilibrium.
Ti concentration in matrix Decreases slowly
with aging time. Far from
equilibrium value of 0.01 at.%
At 0.04 at.% after 64 days.
Concentration changing significantly thus not in equilibrium.
High Temperature Coarsening
Increased Ti in precipitate after double aging
24 hrs. at 300ºC 120 hrs. at 400ºC
Diffusion distance for 64 days at 300ºC: 3 nm
Diffusion distance for double aging treatment: 48 nm
Data for Double Aging Taken with Imago Scienentific LEAP microscope.
Trends in Segregation ofTi to Interface
Segregation increases with aging time at 300ºC Due to slower diffusion in ppt. Interfacial energy is reduced.
Less segregation than Zr Possibly because Ti is more effective at
reducing the lattice parameter. Less segregated after aging at 400ºC
Lower mismatch at higher temperatures.
Room Temperature Strengthening Mechanisms
Orowan looping seems to be the dominant mechanism.
All other mechanisms lead to stresses that would be much too high at the radii measured.
order strengthening modulus mismatch coherency strains
Fairly good agreement with previous studies.1,2
Calculated Orowan Stress
or M 0.4Gb
ln(2r /b)1 v1Marquis EA, Seidman DN, Dunand DC, Acta Mat. 50
(2002) 4021-4035.2Fuller, CB, DN Seidman, DC Dunand, Acta Materialia 51 (2003) 4803-4814.
Creep of Al-0.06 Sc-0.06 Ti at 300ºC
High apparent stress exponents indicative of threshold stress.
For radii in the range 5.8-10.8 nm, creep resistance and threshold stress increases with increasing precipitate size.
At largest average precipitate radius (16.9 nm), however, the interprecipitate distance is so large that the creep resistance has decreased.
RTQA n
th exp)(
Normalized Threshold Stress Most climb related models
predict normalized threshold stress to be constant with radius.
Increase of norm with increasing radius due to lattice and elastic misfits.1
Consistent with Al-Sc, Al-Sc-Mg2 and Al-Sc-Zr3
Slight decrease in creep properties for the Al-Sc-Ti alloy due to lower lattice misfit.
1Marquis EA, Dunand DC, Scripta Mat. 47 (2002) 503-5082Marquis EA, Seidman DN, Dunand DC, Acta Mater. 51 (2003) 4751-4760.3Fuller CB, Seidman DN, Dunand DC, Acta Mater. 51 (2003) 4803-4814.
norm = th/or
Conclusions Ti does not provide as much of a strengthening effect
at room temperature as an equal addition of Sc or Zr to pure aluminum.
Ti partitions to the precipitates, although this is a very slow kinetic process and at the aging times analyzed, most of the Ti remains in solid solution in the matrix.
The coarsening of the precipitates does not agree exactly with coarsening model - slower than predicted.
A creep threshold stress is found at 300ºC, which when normalized by the Orowan stress, increases with increasing precipitate radius. Qualitative agreement is found with a model considering climb with elastic interactions with the precipitate.
