Growth Control of Li 2+x TiO 3+y for an Advanced Tritium Breeding Material The University of Tokyo School of Engineering, Department of Nuclear Engineering and Management Keisuke Mukai (Ph.D. student) , Kazuya. Sasaki, Takayuki Terai, Akihiro Suzuki, Tsuyoshi. Hoshino [email protected]1
26
Embed
Growth Control of Li 2+x TiO 3+y for an Advanced Tritium Breeding Material
Growth Control of Li 2+x TiO 3+y for an Advanced Tritium Breeding Material. Keisuke Mukai (Ph.D. student) , Kazuya. Sasaki, Takayuki Terai , Akihiro Suzuki, Tsuyoshi. Hoshino. The University of Tokyo School of Engineering, Department of Nuclear Engineering and Management. - PowerPoint PPT Presentation
Welcome message from author
This document is posted to help you gain knowledge. Please leave a comment to let me know what you think about it! Share it to your friends and learn new things together.
Transcript
Growth Control of Li2+xTiO3+y for an Advanced Tritium Breeding Material
○High chemical stability & Good Tritium release property ☓Lower Li density than other candidates (ex. Li2O, Li4SiO4)
Li2+xTiO3+y ( Lithium meta-titanate with excess Li )is expected as an advanced breeding material
due to its higher Li density
Background CBBI @PortlandSep. 8
4
β-Li2TiO3 (Monoclinic) phase maintains its phase
1.88 Li/Ti 2.25 ≦ ≦ [1]
Non-stoichiometric lithium titanatewhose Li/Ti ratio is more than 2.0
Li2+xTiO3+y
β-Li2TiO3
+Li4TiO4 β-Li2TiO3
+Li5Ti4O12
51%
Li2O-TiO2Phase diagram
[1] H. Kleykamp, Fusion Engineering and Design 61/62 (2002) 361/366
Li2TiO3
Li2+xTiO3+y
CBBI @PortlandSep. 8What is Li2+xTiO3+y ?
1155℃
5
Li2TiO3
10μm 10μm 10μm
Li-rich
higher densitybigger crystal grain
Li2+xTiO3+y had
SEM images on the cross sections of the sintered pellets at 1200 ℃ for 1h.
but, why ?? 6
CBBI @PortlandSep. 8Previous study
than Li2TiO3
H2 added sweep gas ( 1 ) diffusion in grain( 2 ) desorption at grain boundary( 3 ) diffusion along grain boundary( 4 ) desorption from particle surface and etc.
Li2+xTiO3+y pebble
After T Production, T Behaviors in a blanket are
HTO etc. T
In a blanket with H2 added sweep gas, process(1) is considered as on of a rate determining process[2]
(4)(1)
(2)(3)
CBBI @PortlandSep. 8Tritium residence in the pebbles
[2] M. Nishikawa, A. Baba, Y. Kawamura, Journal of Nuclear Materials 246 (1997) 1-87
H2 added sweep gas
Li2+xTiO3+y pebble
After T Production, T Behaviors in a blanket are
Li2+xTiO3+y pebbles with smaller grains are needed to decrease tritium inventory in the pebbles.
(4)(1)
(2)(3)
d : Grain size [m]DT: The effective diffusivity of tritium in grain (m2/s)θD = d2/60DT
( 1 ) diffusion in grain( 2 ) desorption at grain boundary( 3 ) diffusion along grain boundary( 4 ) desorption from particle surface and etc.
HTO etc. T
[2]
[2] M. Nishikawa, A. Baba, Y. Kawamura, Journal of Nuclear Materials 246 (1997) 1-8
CBBI @PortlandSep. 8Tritium residence in the pebbles
Average residence time under diffusion of T in the crystal grain [s] is
XRD peaks of α-Li2TiO3 and β-Li2TiO3 were calculated by Rietan-FP
002 peak of β-Li2TiO3 is the diffraction from cation layer along c axis
ab
c
a
b
c
CBBI @PortlandSep. 8XRD peak simulation
12
α-Li2TiO3(Cubic)
β-Li2TiO3(Monoclinic)
500℃
700℃
800℃
Inte
nsity
/ a.u
.Powder XRD patterns of the specimens Li2.1TiO3+y sintered at 500-800℃
200
002
-133
All XRD pattern of 500 was attributed to α-Li℃ 2TiO3.
Above 700 , β-Li℃ 2TiO3(Monoclinic) started to formed
CBBI @PortlandSep. 8Crystal structure Li2.1TiO3+y
13
RT XRD patterns of Li2.1TiO3+y were measured after sinterig at 700 ~ 1200℃
Intensity ratio of two peaks were calculated to roughly estimate the existing ratio of α and β phase
002(
β)
-133
(β)
200(
α)
CBBI @PortlandSep. 8Crystal structure Li2.1TiO3+y
14
I002/I-133 was calculated from XRD patterns
Sintering temperature ℃ - β-Li2TiO3 phase mostly formed above 1000 (Li℃ 2TiO3) and above 900 (Li℃ 2.1TiO3+y)
- I002 peak of Li2.1TiO3+y sintered above 1100 became broadened.℃→ This is considered to be due to the stacking fault of α and β phases along c axis.
CBBI @PortlandSep. 8I002/I-133 of Li2TiO3 and Li2.1TiO3+y
15
- β-Li2TiO3 phase fully formed above 1000 (Li℃ 2TiO3) and above 900 (Li℃ 2.1TiO3+y)
I002/I-133 was calculated from XRD patterns
Sintering temperature ℃
- I002 peak of Li2.1TiO3+y sintered above 1100 became broadened.℃→ This is considered to be due to the stacking fault of α and β phases along c axis.
CBBI @PortlandSep. 8I002/I-133 of Li2TiO3 and Li2.1TiO3+y
16
Contents CBBI @PortlandSep. 8
1 Background2 Objective3 Synthesizing Li2+xTiO3+y
4 Crystal structure5 Microstructure6 Summary
17
SEM images ( 2500) on the cross sections of the sintered pellets at 1100☓ ~ 1200 for 1h.℃
CBBI @PortlandSep. 8SEM of Li2TiO3 and Li2.1TiO3+y
18
Significant growth in Li2.1TiO3 1100 →1150 → 1200℃ Gradual growth in Li2 TiO3
Li2TiO3 Li2.1TiO3+y
CBBI @PortlandSep. 8Grain size of Li2TiO3 & Li2.1TiO3+y CBBI @PortlandSep. 8SEM of Li2TiO3 and Li2.1TiO3+y
19
Significant growth in Li2.1TiO3 1100 →1150 → 1200℃ Gradual growth in Li2 TiO3
CBBI @PortlandSep. 8Grain size of Li2TiO3 & Li2.1TiO3+y
Li2.1TiO3+y with small-homogeneous crystal grain at 1100℃Monoclinic Cubic transformation might be related to this phenomena⇔
CBBI @PortlandSep. 8SEM of Li2TiO3 and Li2.1TiO3+y
Li2TiO3 Li2.1TiO3+y
20
CBBI @PortlandSep. 8Summary
The sintering process of Li2TiO3 and Li2.1TiO3+ywere observed by investigating crystal growth and crystal strucuture.
Li2.1TiO3+y specimens sintered above 1100℃ had the larger grain growth than Li2TiO3.From the view point of tritium inventory in ceramic breeder, sintering temperature is needed to be less than 1100℃ .
High temperature XRD and Rietveld analysis are planed to understand the existing ratio of cubic & monocloinic and transformation temperature.
Ordered monoclinic β-phase was obtained above 1000℃ (Li2TiO3) and 900℃ (Li2.1TiO3+y). Above 1100℃, peak broadening were found in Li2.1TiO3+y specimens. → considered to be Cubic + Monoclinic disordering.
21
Thank you for your attention
Portland22
23
Quotation
24
A. Lauman, K. Thomas Felh, et al. Z. Kristallogr 226(2011)53-61
25
Li2MnO3
A. Boulineau, L. Croguennec, et al. Solid State Ionics 180(2010)1652-1659