advanced magnetic tunnel junctions based on cofeb/mgo
TRANSCRIPT
Advanced magnetic tunnel junctions based on CoFeB/MgO interfacial perpendicular anisotropy
Acknowledgement: This work was supported by the project "Research and Development of Ultra-low Power Spintronics-based VLSIs“ under the FIRST Program of JSPS.
SEMATECH 8th International Symposium on Advanced Gate Stack Technology, Session 4: Spin Transfer Torque Memory Bolton Landing, NY 20, October 2011
S. Ikeda1,2 M. Yamanouchi1, H. Sato1, K. Miura3,1,2, K. Mizunuma2, H. Yamamoto3, R. Koizumi2,
H. D. Gan1, S. Kanai2, J. Hayakawa3, F. Matsukura1,2, H. Ohno1,2 1 Center for Spintronics Integrated Systems (CSIS), Tohoku Univ.
2 Laboratory for Nanoelectronics and Spintronics, RIEC, Tohoku Univ. 3 Central Research Laboratory, Hitachi, Ltd.
http://www.csis.tohoku.ac.jp
1
Spintronics devices
2
Nonvolatility High speed operation Virtually unlimited write endurance 1n 10n 100n 1µ 10µ
105
1010
1015
1020
Write time (s)
Flash
FeRAM
PRAM
SRAM/DRAM(Volatile)
MRAM/SPRAM
Num
ber o
f writ
e cy
cles
Magnetoresistive RAMs (MRAMs) SPin transfer torque RAMs (SPRAMs)
Logic-in-memory architecture Reduction of leak current (static power) Reduction of interconnection delay
Memory
Processor core
MTJCMOS
Mochizuki et al., IEICE Transactions on Fundamentals, E88-A (2005) 1408. Matsunaga et al., Appl. Phys. Express, 1 (2008) 091301; ibid., 2 (2009) 023004. Sekikawa et al., IEDM 2008, Suzuki et al., VLSI Technology 2009 Ohno et al., IEDM 2010 Matsunaga et al. VLSI Circuit 2011
(Expectation as low power consumption devices)
MTJWord line
Gate
Bit line
DrainSource
Free
PinnedBarrier
Recording
Reference
1998 2000 2002 2004 2006 2008 2010 2012 2014
Cap
acity
(bits
/chi
p)
Year
MRAM (demo) MRAM (product) SPRAM (i-MTJ)SPRAM (p-MTJ)
1G
1M
10M
100M
100k
10k
1k
100
IBM
Freescale(Motorola)
Sony
Freescale
Samsung
Sony
Toshiba-NEC
Toshiba-NECIBM-Infineon
Everspin
Hitachi-Tohoku Univ.
Cypress
TDK
NTHU-ITRI
ITRI-TSMC-NTHU
Everspin
NECToshiba Hynix-Grandis
MRAM development
2Mb SPRAM ISSCC 2007
Kawahara et al., IEEE J. Solid-State Circuits 43 (2008) 109.
Cross section SEM image
of SPRAM cell
MTJ cells
M3
M2
M1CMOS-Tr.
M4
50 nm
Recording layer
MTJ cell
Lower electrode
pinned layerAnti-ferromagnetic layer
MgObarrier
32Mb SPRAM
VLSI Circuit 2009 Takemura et al., IEEE J. Solid-State Circuits 45 (2010) 869.
Ikeda et al., IEEE Trans. Electron Devices, 54 (2007) 991.
SA & Write
128kbArray
Word D
river/Dec.
Control CircuitsPre-Decoder
Y-Dec.
Magnetic field
Spin transfer torque
3
Nonvolatile circuits for logic-in-memory
Matsunaga, …Hanyu et al., Appl. Phys. Express 1 (2008) 091301.
MTJ-Based Nonvolatile Full Adder
Matsunaga, ... Hanyu et al., Appl. Phys. Express 2 (2009) 023004.
MTJ-Based Nonvolatile Ternary Content- Addressable Memory (TCAM) cell
MTJ-Based Nonvolatile Lookup-Table Circuit Chip
Suzuki, …Hanyu,et al., VLSI Circuit Symposium 2009.
2-kbTCAM
cell array
Column Dec.
Row
Dec
.
Sens
e A
mp.
174 µm
2kb-nonvolatile TCAM chip
Matsunaga, …Hanyu,et al., VLSI Circuit Symposium 2011.
4
Technology issues toward realization of nonvolatile VLISs
High output (TMR ratio>100%)
Low switching current (IC < F μA)
Thermal stability for nonvolatility (E/kBT > 40) Annealing stability in back-end-of-line process (Ta > 350oC)
+ Scalability
To realize nonvolatile VLISs (MRAM and logic-in-memory) using the leading edge technology node, there are still issues to be addressed. ISSUES
• MTJs have to satisfy these requirements with scalability at the same time. • In order to satisfy these requirements, we focus on the MTJs with
perpendicular anisotropy electrodes.
5
Progress of MTJs CoFeB
MgO CoFeB
bcc (001)
rock salt (001)
bcc(001)
0
100
200
300
400
500
600
700
1994 1996 1998 2000 2002 2004 2006 2008 2010
トンネル
磁気抵抗比
(%)
年
AlOx-barrier MTJs
CanonANELVA & AIST
AIST
Tohoku Univ. & Hitachi
604%@RT(1144%@5K)
IBMAIST
AIST
TMR
ratio
(%)
Tohoku Univ.
MgO-barrier MTJs
Year
S. Ikeda et. al., Appl. Phys. Lett. 93, 082508 (2008). Nat. Mat., 9, 721 (2010)
SiO2/Si sub.
Ta(5) Ru(10) Ta(5)
CoFeB(5 ) →
MgO(2.1) CoFeB(6) →
Ta(5) Ru (5) Cr/Au
Cr/Au
SiO2/Si sub.
Ta(5) Ru(10) Ta(5)
CoFeB(1 ) ↑ MgO(0.9)
CoFeB(1.7) ↑ Ta(5) Ru (5)
Cr/Au
In-plane anisotropy pseudo-SV
Perpendicular anisotropy pseudo-SV
6
M-H curves of CoFeB/MgO stack samples with different tCoFeB
-1
0
1
-0.5 0.0 0.5 1.0
-1
0
1
tCoFeB = 2.0 nm
in-plane out-of-plane
M
(T)
tCoFeB = 1.3 nm
µ0H (T)
In-plane anisotropy
Perpendicular anisotropy
Ta=300oC
Ta=300oC
CoFeB(tCoFeB ) MgO(1)
SiO2/Si sub. Ta(5)
Ru(10) Ta(5)
µ0Hs_in-plane = 0.34 T Ms = 1.58 T K = 2.1x105 J/m3
S. Ikeda et al., Nat. Mat. 9 (2010) 721.
Ta=300 oC, 4 kOe, 1h
7
0 1 2-1
0
1
K
⋅ tCo
FeB (
mJ/
m2 )
tCoFeB (nm)
VSMFMR
in-plane
Perpendicular
tCoFeB dependence of KtCoFeB in CoFeB/MgO stack
CoFeB(tCoFeB ) MgO(1)
SiO2/Si sub. Ta(5)
Ru(10) Ta(5)
KtCoFeB = (Kb-MS2/2µ0) tCoFeB+Ki
•From the y-intercept, Ki = 1.3 mJ/m2. •The CoFeB/MgO interfacial anisotropy Ki is dominant in the perpendicular anisotropy because Kb is negligible.
Ta = 300oC
S. Ikeda et al., Nat. Mat. 9 (2010) 721. 8
tMgO dependence of Ms and K
1 monolayer of MgO is ~0.21 nm
More than 3 monolayers of MgO is required to stabilize the perpendicular anisotropy induced by CoFeB-MgO interface.
Saturation magnetization Ms and effective magnetic anisotropy energy density K are evaluated from the out-of-plane M-H curves.
0.0
0.4
0.8
1.2
0.0 0.5 1.0 1.5 2.00.00.51.01.52.0
Ms (
T)
K (1
05 Jm
-3)
tMgO (nm)
tMgO = 0.6 nm
M. Yamanouchi et al., J. Appl. Phys. 109 (2011) 07C712.
0.42 nm
Mg O
9
anti-bonding
bonding
O 2pZ
σ-coupling
23z
dzp2O Fe
Fe 3dz2 (m=0)
K. Nakamura et al., Phys. Rev. B, 81 (2010) 220409. R. Shimabukuro et al., Physica E 42 (2010) 1014.
23z
d : in-plane anisotropy
(m=0)
Possible factor of the perpendicular anisotropy in CoFeB/ MgO stack
• 3dz2 band of Fe is pushed up above the Fermi energy.
• The contribution of 3dz2 orbital of Fe becomes small,
resulting in appearance of perpendicular anisotropy.
10
TMR properties in CoFeB-MgO p-MTJs
-0.2 -0.1 0.0 0.1 0.210
20
30
40
50
R (k
Ω)
µ0H (T)
Ta = 300oC
Clear hysteresis -> top and bottom CoFeB electrodes have perpendicular anisotropy.
SiO2/Si sub.
Ta(5)Ru(10)Ta(5)
CoFeB(0.9 )
MgO(0.9)CoFeB(1.5 )
Ta(5)Ru (5)Cr/Au
Al2O3
V-
V+
(nm)
40 nm
Parallel
Antiparallel
S. Ikeda et al., Nat. Mat. 9 (2010) 721. 11
Junction size dependence of Ic0
Ic0 linearly decreases with junction area S (volume Vrec). We confirmed scalability of switching current for spin transfer torque. 50 nm
SiO2/Si sub.
Ta(5) Ru(10) Ta(5)
CoFeB(0.9 )
MgO(0.9) CoFeB(1.5)
Ta(5) Ru (5) Cr/Au
F = 40 ~ 76nmφ Ta=300oC w/o Hex
0 1000 2000 3000 4000 5000 6000-100
-50
0
50
100
150
200
IC0 (P to AP) IC0 (AP to P)
Critic
al c
urre
nt, I
C0 (µ
A)
Recording layer volume, Vrec (nm3)
76 nm70 nm59 nm
44 nm53 nm
Junction size
= S・tCoFeB
H. Sato et al., Appl. Phys. Lett. 99 (2011) 042501. 12
Junction size dependence of E/kBT
0 1000 2000 3000 4000 5000 60000
20
40
60
80
pulse current experiment pulse field experiment previous report
Ther
mal
sta
bility
fact
or, E
/kBT
Recording layer volume, Vrec (nm3)
76 nm70 nm59 nm
44 nm53 nm
Junction size
E/kBT maintained almost constant values even though the junction diameter was varied from 40 nm to 80. IC0 reduces in proportion to the volume of the recording layer but the E/kBT values are not affected much by the volume down to 40 nm in diameter.
= S・t
H. Sato et al., Appl. Phys. Lett. 99 (2011) 042501. 13
Origin of the junction size dependence of IC0 and E/kBT
Nucleation embryo
Nucleation type magnetization reversal
0 20 40 60 80 1000
20
40
60
80
Effe
ctive
diam
eter
, Dn (
nm)
Junction size in diameter (nm)
No clear reduction in E/kBT with different junction size
Dn showed almost constant values of 40 nm in diameter, which is almost independent of junction size.
Nucleation diameter: Dn
IC0=JC0S=JC0(π(D2-Dn2)/4)+π(Dn/2) 2)∝S
E/kBT=Keffπ(Dn/2) 2/kBT ∝Dn2
Junction area (diameter): S (D)
Nuc
leat
ion
diam
eter
, Dn (
nm)
H. Sato et al., Appl. Phys. Lett. 99 (2011) 042501. 14
Jc0 and E/kBT of MTJs with 40 nm diameter
40 nm Ta(oC) TMR ratio (%)
RA (Ωµm2)
Jc0 (MA/cm2) E/kBT
300 124 18 3.9 43.1 350 113 16 3.8 39.1
w/o Hex
w/o Hex
Ta=300oC
Ta=350oC
S. Ikeda et al., Nat. Mat. 9, (2010) 721. K. Miura et al., MMM 2010, HC-02.
•Jc0 and E/kBT are maintained after annealing at 350oC. •This MTJ system has a back end of the line (BEOL) compatibility.
SiO2/Si sub.
Ta(5)Ru(10)Ta(5)
CoFeB(1.0 )MgO(0.85)CoFeB(1.7)
Ta(5)Ru (5)Cr/Au
Al2O3 Al2O3
15
Comparison of MTJs Type Stack structure
(nm) Size (nm)
MR (%)
RA (Ωμm2)
JC0 (MA/cm2)
IC0 (μA) Δ=E/kBT IC0/Δ Ta (oC) Ref.
i-MTJ CoFeB(2)/Ru(0.65)/CoFeB(1.8) SyF 100x200 >130 ~10 2 ~400 65 ~6.2 300-
350 J. Hayakawa et al., IEEE
T-Magn., 44, 1962 (2008)
p-MTJ L10-
FePt(10)/Fe(t)/Mg(0.4)/ MgO(1.5)/L10-FePt(t)
Blanket 120 (CIPT)
11.8k - - - - 500 M. Yoshizawa et al.,
IEEE T-Magn., 44, 2573 (2008)
p-MTJ L10-
FePt/CoFeB/MgO(1.5)/ CoFeB/Co based
superlattice
Blanket 202 (CIPT)
- - - - - - H. Yoda et al.,
Magnetics Jpn. 5, 184 (2010) [in Japanese].
p-MTJ [Co/Pt]CoFeB/CoFe/MgOCoFe/CoFeB/TbFeCo Blanket 85-97
(CIPT) 4.4-10 - - - - 225 K. Yakushiji et al., APEX
3, 053033 (2010)
p-MTJ [CoFe/Pd]/CoFeB/MgO/CoFeB/[CoFe/Pd]
800x800N
100 (113)
18.7k (20.2k) - - - - 350
(325) K. Mizunuma et al.,
MMM&INTERMAG2010
p-MTJ CoFeB (1)/ TbCoFe (3) 130 φ ~15 4.7 650 107 6.08 - M. Nakayama et al., APL 103, 07A710 (2008)
p-MTJ L10-alloy 50-55 φ - - - 49 56 0.88 - T. Kishi et al., IEDM 2008
p-MTJ Fe based L10 (2)/CoFeB (0.5) - - - - 9 - - -
H.Yoda et al., Magnetics Jpn. 5, 184 (2010) [in
Japanese].
p-MTJ CoFeB/MgO/CoFeB 40 φ 113
(124) 16
(18) 3.8
(3.9) 48
(49) 39
(43) 1.23 (1.14)
350 (300)
S. Ikeda et al., Nat. Mat. 9 (2010) 721.
K. Miura et al., MMM2010,HC-02
These p-MTJ technologies will be a promising building block for nonvolatile VLSIs using spin-transfer torque switching.
16
Issue for p-MTJs
Slide 17
Parallel state Low resistance
Antiparallel state High resistance
Different polarity =Stable
The same polarity =Unstable
Free
Reference
N
S
N
S
N
S
N
S
The thermal stability ∆p=E/kBT of anti-parallel state in p-MTJs becomes low by comparison with parallel state.
Bit Information “0” Bit Information “1”
17
Enhancement of thermal stability ∆P, AP = ∆ [1±Hs/Hc0]2
Free
Reference
Hs
E/kBT
“1” “0” ∆AP ∆P
Hs decreases by employing step structure with large reference layer. ∆AP increases with decreasing diameter of reference layer.
Hs “1” “0”
∆AP ∆P
E/kBT Free
Reference
Stepped structure
Conventional structure
dipole interlayer coupling field
18
Two types of p-MTJs
Slide 19
100 nm
F = 100 nm
CoFeB
CoFeB
MgO
F = 100 nm
300 nm
CoFeB
CoFeB
MgO
100 nm
Stepped structure Conventional structure
F : Feature size
Free layer
Reference layer
K. Miura et al., 2011 VLSI Technology, 11B-3.
1.5 nm 0.9 nm 0.9 nm
1.5 nm 0.9 nm 0.9 nm
19
Hs in two types of p-MTJs
Slide 20
Hs
Stepped structure Conventional structure
Hs
Conventional structure Stepped structure
TMR ratio (%) 100 97 RA (Ωµm2) 13 13
Hs (mT) 22 5
1
2
3
4
-100 -50 0 50 100
Res
ista
nce
(kΩ
)
Magnetic field (mT)
1
2
3
4
-100 -50 0 50 100
Res
ista
nce
(kΩ
)
Magnetic field (mT)
Hs can be reduced by using stepped structure. K. Miura et al., VLSI Technology 2011, 11B-3. 20
∆P and ∆AP in two types of p-MTJs
∆AP in stepped structure increases.
Conventional structure Stepped structure ∆P 71.2 72.9 ∆AP 46.5 70.1
Stepped structure Conventional structure “P”->”AP” “AP”->”P” “P”->”AP” “AP”->”P”
00.20.40.60.8
1
-150 -75 0 75 150
Prob
abili
ty
Magnetic field (mT)
00.20.40.60.8
1
-150 -75 0 75 150
Prob
abili
ty
Magnetic field (mT)
∆P,AP
K. Miura et al., VLSI Technology 2011, 11B-3. 21
Cell area of stepped structure
Cell area of 0.09 µm2 (300nmφ) in the stepped structure corresponds to SRAM cell area at 32 nm technology node. Cell area can be down to 0.04 µm2 (200nmφ) without degrading the retention time over 10 years, which corresponds to SRAM cell area at 20 nm technology node.
0.01
0.1
1
10
0 50 100 150
Cel
l are
a (µ
m2 )
Technology node (nm)
32 nm 300 nm
CoFeB
CoFeB
MgO
F = 100 nm
20 nm
SRAM 100F2 (F: feature size)
F = 100 nm
200 nm
CoFeB
CoFeB
MgO
K. Miura et al., VLSI Technology 2011, 11B-3. 22
Summary We have demonstrated that the critical current Ic0 in CoFeB/MgO
perpendicular anisotropy MTJs (p-MTJs) can be scaled down with decreasing recording layer volume.
The thermal stability factor E/kBT can be maintained at about 40 even though the recording volume was reduced to 40 nm. The magnetization reversal in CoFeB/MgO p-MTJs is dominated by nucleation type magnetization reversal (nucleation diameter ~40 nm).
CoFeB/MgO p-MTJs show the high TMR ratio of more than 100%, high thermal stability at dimension as low as 40 nm diameter and a low switching current of 49 μA at the same time .
CoFeB/MgO p-MTJ with step structure shows the enhancement of thermal stability in antiparallel state, which achieves thermal stability for data retention time over 10 years.
23