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Symposium on Materials ChallengesFor Safety and Reliability y y
4th World Materials Research Institute ForumIMR-CAS, Shenyang
Biomedical titanium alloys for improved implant reliability and compatibility
Rui Yang, Yulin Hao and Shujun Lig, j
Shenyang National Laboratory for Materials ScienceInstitute of Metal Research, Chinese Academy of Sciences
23 May 2011
Earliest application of biomedical materials
• Artificial toe made of wood and leather found on a mummyD t d t l t 4000• Dated at least 4000 years ago
• Used by its carrier for both aesthetic and functional values
2
Current problem of orthopaedic implants Stress shielding: Reduction in bone stress in vivo following the introduction of orthopaedic implants and it causes loss of bone and loosening of the implant.
Statistical significance of correlation between severe t hi ldi d i i fl i f t
3
stress shielding and various influencing factors.
Z. Wan, L.D. Dorr, T. Woodsome, A. Ranawat and M. Song, J. Arthroplasty 1999; 14: 149
The alternative design does not work
Overhauling implant design has greater effect on stress distribution than anything possible by altering material properties but newthan anything possible by altering material properties, but new
design is not considered safe(bars show changes in absolute values of the major principal strains,
% of the intact femur, after implantation)
4R. Decking, W. Puhl, U. Simon, L.E. Claes, Clin. Biomech. 2006; 21: 495
% of the intact femur, after implantation)
mented and cementless implant
Survival of cemented and cement-less hip prostheses in Finland (1985 1999)
portunities for low-modulus implant materials
alleviate short-m/long-term designm/long term design nflict
reduce sensitivity of plant performance to
dividual factors
allow incrementalallow incremental provement to current signs
Survival of hip prostheses in Finland 1985-1999, by age of patient
anium alloys as implant materials: story and current problemsstory and current problems
ee generations of development: Problems to be solved:g pTi-6Al-4V (Aerospace alloy)Ti-6Al-7Nb (Removes poisonous elements)
(by alloy design)1. Some alloys still contain
i l t ( Al)Ti-13Nb-13Zr (To reduce modulus) poisonous elements (e.g., Al)2. Elastic modulus still too
high compared to human ar 7 alloys are approved by M for surgical implant (only 3 roved in China *):
ghard tissue
(by surface engineering)1 Bi ti it t id lTi *
Al-4V *Al-2.5V
1. Bioactivity not ideal2. Relatively poor wear
resistanceAl-7Nb*F
3. Corrosion resistance can be further improved
st recent developments: m Metal (Toyota) vs Ti2448 (IMR)m Metal (Toyota) vs. Ti2448 (IMR)
Ti2448 Gum MetalTi2448 Gum Metal
P ti Ti2448 G M t l
H. Ikehata et al. MRS Bullitin 2006; 31: 688et al., Acta Biomater. 2007; 3: 277.
Properties Ti2448 Gum MetalElectron/atom ratio 4.15 4.24Dynamic modulus (GPa) 40 42 55 65
ta type biomedical titanium alloys: mmary of recent developmentmmary of recent development
Ti-29Nb-13Ta-4.6Zr Ti-15Mo
Ti-13Nb-13ZrTi-35Nb-5Ta-7Zr
GUM METALTi-12Mo-6Zr-2Fe
Ti-15Mo-3Nb-0.3O
"
Ti-V Ti-Nb Ti-Mo
Ti 24Nb 4Z 8S
Fedotov, Proc. of 2nd World erence on Titanium (1973)
ficulty in reducing elastic modulus
MetalsAlloys
GraphiteCeramicsSemicond
Composites/fibers
strength and elastic ulus of metals tend to ease or decrease
Al oxide Carbon fibers only
600800
10001200
400 TungstenSi carbide
Diamond
ySemicond
Ti
ultaneously
ngth must be maximised
Platinum
Silver Gold
Tantalum
Zinc, Ti
Steel, NiMolybdenum
Si crystal
Gl d
Si nitrideAl oxide Carbon fibers only
Aramid fibers only
80100
200
400
Cu alloys
Tungsten
<100>
<111>
AFRE(|| fibers)*
CFRE(|| fibers)*
Ti: ~110GPa
rder to ensure the ue life and thus the bility of the implant
Magnesium,AluminumSilver, Gold Glass-soda
Concrete
CFRE*
GFRE*
Glass fibers only
20
406080
Tin GFRE(|| fibers)*
AFRE(|| fibers)
Bone:
hanisms such as stress-ced martensitic sformation are
8Graphite
AFRE( fibers)*
CFRE*
46
10
Polyester
PSPET
CFRE( fibers)*
GFRE( fibers)*Bone: <30GPa
sformation are ficient in this task
problem must be
1
PC Epoxy only
0 8
2
HDPEPP
PS
E GP
problem must be led from a more amental level
k modulus of Ti-TM binary alloys: Predictions
method was proposed to estimate the bulk modulus of Ti-TM nary alloys based on first principles computationnary alloys based on first principles computation
followed by Nb, Ta, was predicted to lower the bulk modulus of c Ti
oice of primary binary system: Ti-Nb
does not change the e/a ratio of Ti (same group)is high melting thus difficult to process and also too expensiveNb is a suitable primary system: intrinsic minimum of E at e/a ~4.15
4 wt.% Nb)Ti-NbTi Nb
moving the modulus peak
Both Zr and Sn reduce Ms for "wt.% of Nb, Zr, Sn reduces Ms by 7 6K 41 2K 40 9K ti l7.6K, 41.2K, 40.9K, respectivelyr + Sn suppress the r and Sn are potent strengtheners for i alloy
Alloy T, C MS, C Phase E, GPa
Ti-24Nb ~700 380~400 ++ ~90
ect of alloying on phase stability: Computation
A+first principles mputation enable sonably accurate atment of solid
tiutionsth Nb and Sn are bilizing elements h respect to the ase and can vent formation of phases neutral
ect of Sn on elastic properties of 24Nb 4Z b d ll24Nb-4Zr based alloysminimum of bulk modulus (B) and Poisson’s ratio () at 9wt % Sn was identified9wt.% Sn was identifiedr the 7.9wt.%Sn alloy, the bulk modulus (B) approximately uals the shear modulus (G)
50
60
0 30
0.35E Depending on impurity
40
50
0.25
0.30
B
Poisso
Bulk modulus:17-24 GPaShear modulus:21-23 GPa
contents and heat treatment:
20
30
0.15
0.20
Gon's rat
Shear modulus:21-23 GPaYoung’s modulus:40-50 GPaPoisson’s ratio:0.09-0.14
7.5 7.6 7.7 7.8 7.9 8.0 8.1 8.210 0.10
G io
S t t %
B G E/2
astic modulus of Ti2448 single crystals
E011
E001
E111
E011E001
Ti V
E111
4 0 4 2 4 4 4 6 4 84 2 4 4 4 6 4 8
Ti-V Ti-Cr Ti-Nb
4 0 4 2 4 4 4 6 4 84.0 4.2 4.4 4.6 4.8
Electron/atom (e/a) ratio4.2 4.4 4.6 4.8
ectron/atom (e/a)ratio
G011
G111
G001
4.0 4.2 4.4 4.6 4.8
Electron/atom (e/a) ratio
011
111
Ti V
001
Ti-V Ti-Cr Ti-Nb
chanical properties of Ti2448
ery short linear elastic stage; mostly non-linear elatic deformation; bsence of “double yielding”y glastic strain recovery of 3.3% occurs at 4% applied strainensile strength ~850MPaignificant elastic softening was found (decrease of incipient Young’significant elastic softening was found (decrease of incipient Young s
modulus with prestraining)1000
65
600
80065
43
MP
a) 42GPa33GPa
850 MPa
400
6002
tress
(M
1
18GPa
0
200S 1
ay and TEM show large elastic deformation
>3% elasticity confirmed by x-ray measurementTEM observed significant recoverable lattice distortion
8000
1%
Unloading after 4% strain
4000
6000 1%2%3%4%
Before loading
2000
37.5 38.0 38.5 39.0 39.50
(110) diffraction peaks
2, Degree
.L. Hao et al., Phys. Rev. Lett. 2007; 98: 216405
situ neutron diffraction analyses
2.0
2.5
y
5MPa 159MPa350MPa
(110)• Below ~500 MPa (200) spacing
change contributes more to the
1.0
1.5
y 350MPa 396MPa 472MPa 537MPa 594MPa
change contributes more to the reversible strain
• Above 500 MPa (110) spacing change contributes more
2.10 2.15 2.20 2.25 2.30 2.35 2.40 2.45
0.5 650MPa
change contributes more• Switchover at ~1.5%
Lattice spacing, nm/10
600
700
300
400
500
600
s, M
Pa
100
200
300 (110) (200)SpecimenSt
ress
plications of B≈G in crystals
Lowest bulk modulus (23.9 GPa) of known structural metalsLowerest Poisson’s ratio (0.14) second only to Be
•The bulk modulus B measures resistance to bond breaking
•The shear modulus G measures•The shear modulus G measures resistance to bond angle change (bending)F t t l d ll B G•For most metals and alloys B > G
onsequence of low B: Large elastic lattice stretching
servation of amorphization and no crystal formation during compressionno crystal formation during compression
ghly localised plastic deformation
~[111] [ ]
ntation m
1m
1m~[113]
m
Intersection and extension of shear bands leading to refinement of coarse grains to tens nanometer
w mechanisms of elastic deformation d grain refinement
Alloy B (GPa) G (GPa)
d grain refinement
4Nb-4Zr-7.9Sn 23.9 22.7 0.144Nb-4Zr-7.6Sn 43 21 0.29
er Sn contentscreate a more favourable condition for slipenable martensitic transformation (”)
u stretching experiment under TEM found that, i i t i 3 h i f l ti
enable martensitic transformation ( )
increasing strain, 3 mechanisms of elastic rmation operate:
fy planar lattice
ti
Reversible motion of dislocation loops
nucleated
Stress-induced martensitic
t f ti
situ observation of homogeneous nucleation d reversible movement of dislocationsd reversible movement of dislocations
om dipoles to disclinations: A mechanism of pid nano grain formationpid nano-grain formation
ect of low modulus and high elasticity:ramedullary nails on fractured tibiaramedullary nails on fractured tibia
Ti2448Ti-6Al-4V
448 Ti-6Al-4V l out force:l out force:
7.9N 110.9N
ne volume fractions:8% 32 6%8% 32.6%
Micro-CT analysis
gh cycle fatigue properties of Ti2448
gue strength/yield strength ratio 0.50.6,similar to conventional beta titanium alloystitanium alloys
gue strength can be improved by heat treatment and TMPm rolling + triple heat treatment improves fatigue strength to >1000MPa
500
600
a
As-forged1000
1100
1200
a
R=0.1
400 re
ss, M
Pa
R=0.1800
900
1000
ess,
MPa
Warm rolling Warm rolling + aging
104 105 106 107200
300R=-1
Str
104 105 106 107500
600
700Stre
10 10 10 10 N
104 105 106 107
N
lationship of fatigue strength to Young’s dulus of titanium alloys
1200a
dulus of titanium alloys
1000
1200Ti2448-O(WR+HT)
, MP
a
R = 0.1
600
800 Ti2448-O(WR)
engt
h,
400
600
type alloysTi2448(WR)
ue s
tre
0 20 40 60 80 100 1200
200 type alloys CP-Ti
Fatig
u
0 20 40 60 80 100 120F
Young's modulus, GPa
ain-controlled low cycle fatigue of Ti2448
6
%
R=0.3 R=0.1 R=-1R=0.1(Ti-39Nb-13Ta-4Zr)
(a)
4
5
m st
rain
, %
( )
2
3
Max
imum
5.05.5
(b) R=0.3 R=0.1 R=-1R=0.1(Ti-39Nb-13Ta-4Zr)
4(c) R=0.3 R=0.1 R=-1
R=0 1(Ti-39Nb-13Ta-4Zr)
100 101 102 103 104 1052
Reversals to failure, 2Nf
3 03.54.04.5
stra
in, %
R 0.1(Ti 39Nb 13Ta 4Zr)
2
3
stra
in, %
R=0.1(Ti-39Nb-13Ta-4Zr)
2.02.53.0
Ela
stic
1
Plas
tic
w notch sensitivity of Ti2448
600
700
MPa
smooth Kt=3Kt=3 5
R = 0.1
300
400
500
ic st
ress
, M
Kt=3.5 Kt=4
105 106 107100
200Cyc
li
N b f l t f il
Material K =3 r=0 34 K =3 5 r=0 28 K =4 r=0 14Notch sensitivity factor q in the range 106 cycles
Number of cycles to failure
Material Kt=3, r=0.34 Kt=3.5, r=0.28 Kt=4, r=0.14
Ti2448 (R=-1) 0.37 0.27 0.27
Ti2448 (R=0 1) 0 33 0 35 0 26Ti2448 (R 0.1) 0.33 0.35 0.26
Ti2448 (R=0.3) 0.30 0.28 0.26
Ti 13Nb 13Z 0 78 0 70 0 79
gh threshold / low crack propagation rate
1E-3
ycle
)
1E-5
1E-4
N
(mm
/cy
TC4 Ti Ti2448(R=0.1)
10 20 30 40 50 601E-6da
/dN
K (MP / 1/2)
100µm100µm
Pure Titanium
500µm
K (MPa/m1/2)1E-4
cycl
e)
Ti2448 alloy
1E-5 N
(mm
/c
500µm500µm 100nm100nm
Ti2448 alloy 25 30 35 40 451E-6da
/dN
K (MP / 1/2)
200µm
ack growth experiments
000 cycles 1 000 000 l300 000 l,000 cycles 1,000,000 cycles300,000 cycles
plication
February 2008: Tests of biochemical compatibility authorised by the State Food and Drug Administration of China completed
June 2009: Clinical trials of bone plates and nails in human body completed
M h 2010 Cli i l t i l f i l fi ti l t dMarch 2010: Clinical trials of spinal fixation completed
nical trials: Ankle bone repair
nical trials: Shoulder bone repair
nical trials: Tibia repair
nical trials: Spinal fixation
mmary
A new titanium alloy Ti2448 for biomedical use was developed– High strength (850 MPa) /excellent fatigue properties– Lowest bulk modulus of structural metals (23.9 GPa), and incipient
Young’s modulus almost matching that of human bone (~40 GPa)– Superelastic deformation up to 3.3%– Good biocompatibility
New mechanisms of elastic deformation: lattice distortionNew mechanisms of elastic deformation: lattice distortion, reversible motion of dislocation loops nucleated homogeneously
The alloy has passed biochemical compatibility tests authorised by e a oy as passed b oc e ca co pat b ty tests aut o sed bythe State Food and Drug Administration of China, and has completed clinical trials of typical implants in hospitals
Low modulus ensures improved biomechanical compatibility and safety of implants; High recoverable strain enables high fatigue strength and thus improves life-time and reliability
knowledgements
G d t St d tGraduate StudentsDr Caiyun Zheng, Dr Yanwei Zhang, Dr Siqian Zhang, Dr Edward G. ObbardDr Edward G. Obbard
Collaboration withWego GroupProfessor Zheng Guo, The Fouth Military Medical University Professor Yue Zhu, China Medical UniversityProfessor Yue Zhu, China Medical UniversityProfessor Manling Sui, Beijing Polytechnical University
Funding fromMoST 973 grant 2006CB605104