LETTERS

High-performance lithium battery
anodes using silicon nanowires
CANDACE K. CHAN1, HAILIN PENG2, GAO LIU3, KEVIN McILWRATH4, XIAO FENG ZHANG4,ROBERT A. HUGGINS2 AND YI CUI2*
1

Department of Chemistry, Stanford University, Stanford, California 94305, USA
Department of Materials Science and Engineering, Stanford University, Stanford, California 94305, USA
3
Environmental Energy Technologies Division, Lawrence Berkeley National Lab, 1 Cyclotron Road, Mail Stop 70R108B, Berkeley, California 94720, USA
4
Electron Microscope Division, Hitachi High Technologies America, Inc., 5100 Franklin Drive, Pleasanton, California 94588, USA*e-mail: yicui@stanford.edu
2

Published online: 16 December 2007; doi:10.1038/nnano.2007.411

There is great interest in developing rechargeable lithium
batteries with higher energy capacity and longer cycle life forapplications in portable electronic devices, electric vehicles
and implantable medical devices1. Silicon is an attractive
anode material for lithium batteries because it has a low
discharge potential and the highest known theoretical charge
capacity (4,200 mAh g21; ref. 2). Although this is more thanten times higher than existing graphite anodes and muchlarger than various nitride and oxide materials3,4, silicon
anodes have limited applications5 because silicon’s volume
changes by 400% upon insertion and extraction of lithium,which results in pulverization and capacity fading2. Here, weshow that silicon nanowire battery electrodes circumvent theseissues as they can accommodate large strain without
pulverization, provide good electronic contact and conduction,and display short lithium insertion distances. We achieved thetheoretical charge capacity for silicon anodes and maintained adischarge capacity close to 75% of this maximum, with little
fading during cycling.
Previous studies in which Si bulk films and micrometre-sizedparticles were used as electrodes in lithium batteries have shown
capacity fading and short battery lifetime due to pulverizationand loss of electrical contact between the active material and thecurrent collector (Fig. 1a). The use of sub-micrometre pillars6
and micro- and nanocomposite anodes5,7–9 led to only limited
improvement. Electrodes made of amorphous Si thin films have astable capacity over many cycles5,8, but have insufficient material
for a viable battery. The concept of using one-dimensional (1D)
nanomaterials has been demonstrated with carbon10, Co3O4(refs 11, 12), SnO2 (ref. 13) and TiO2 (ref. 14) anodes, and has
shown improvements compared to bulk materials. A schematic of
our Si nanowire (NW) anode configuration is shown in Fig. 1b.
Nanowires are grown directly on the metallic current collector
substrate. This geometry has several advantages and has led to
improvements in rate capabilities in metal oxide cathodematerials15. First, the small NW diameter allows for betteraccommodation of the large volume changes without theinitiation of fracture that can occur in bulk or micron-sizedmaterials (Fig. 1a). This is consistent with previous studies thathave suggested a materials-dependent terminal particle size below
which particles do not fracture further16,17. Second, each Si NW

is electrically connected to the metallic current collector so that
all the nanowires contribute to the capacity. Third, the Si NWs
have direct 1D electronic pathways allowing for efficient chargetransport. In electrode microstructures based on particles,
electronic charge carriers must move through small interparticle
contact areas. In addition, as every NW is connected to thecurrent-carrying electrode, the need for binders or conducting
additives, which add extra weight, is eliminated. Furthermore,nature nanotechnology | VOL 3 | JANUARY 2008 | www.nature.com/naturenanotechnology

31

Initial substrate

After cycling
X

Film
X

X

Particles

Nanowires

Efficient 1Delectron transport

Facile strain
relaxation

Good contact with current collector

Figure 1 Schematic of morphological changes that occur in Si during
electrochemical cycling. a, The volume of silicon anodes changes by about
400% during cycling. As a result, Si films and particles tend to pulverize during
cycling. Much of the material loses contact with the current collector, resulting
in poor transport of electrons, as indicated by the arrow. b, NWs grown directlyon the current collector do not pulverize or break into smaller particles after
cycling. Rather, facile strain relaxation in the NWs allows them to increase indiameter and length without breaking. This NW anode design has each NW
connecting with the current collector, allowing for efficient 1D electron transport
down the length of every NW.

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2.0
72

Potential versus Li/Li + (V)Discharge

Current (mA)

1
0
1
–2

Charge

–4

7

–6
0.0

0.5

1.5
1.0
0.5
0.0

1.0

1.5

0

2.0

1,000 2,000 3,000 4,000 5,000

Potential versus Li/Li+ (V)Capacity (mAh g–1)

C/20

4,000
Capacity (mAh g–1)

Potential versus Li/Li + (V)C/10
C C/2 C/5

2.0
1.5
1.0
0.5

C/10 C/20
0.0

C C/2 C/5
0

1,000
2,000
3,000
Capacity (mAh g–1)

3,000
Si NW charge
Si NW discharge
Si NC charge
Graphite charge

2,000
1,000
0

4,000

0

2

4
6
Cycle number

8

10

Figure 2 Electrochemical data for Si NW electrodes. a, Cyclic voltammogram for Si NWs from 2.0 V to 0.01 V versus Li/Liþ at 1 mV s21 scan rate. The first sevencycles are shown. b, Voltage profiles for the first and second galvanostatic cycles of the Si NWs at the C/20 rate. The first charge achieved the theoretical capacityof 4,200 mAh g21 for Li4.4Si. c, The voltage profiles for the Si NWs cycled at different power rates. The C/20 profile is from the second cycle. d, Capacity versus
cycle number for the Si NWs at the C/20 rate showing the charge (squares) and discharge capacity (circles). The charge data for Si nanocrystals (triangles) fromref. 8 and the theoretical capacity for lithiated graphite (dashed line) are shown as a comparison to show the improvement when using Si NWs.

our Si NW battery electrode can be easily realized using thevapour–liquid –solid (VLS) or vapour–solid (VS) template-free
growth methods18–23 to produce NWs directly onto stainless steel
current collectors (see Methods).
A cyclic voltammogram of the Si NW electrode is shown in
Fig. 2a. The charge current associated with the formation of the
Li–Si alloy began at a potential of 330 mV and became quite
large below 100 mV. Upon discharge, current peaks appeared atabout 370 and 620 mV. The current–potential characteristics wereconsistent with previous experiments on microstructured Si
anodes6. The magnitude of the current peaks increased withcycling due to activation of more material to react with Li in each
scan6. The small peak at 150–180 mV may have been due toreaction of the Li with the gold catalyst, which makes a negligible
contribution to the charge capacity (see Supplementary
Information, Figs S1 and S2).
Si NWs were found to exhibit a higher capacity than otherforms of Si (ref. 5). Figure 2b shows the first and second cycles at
the C/20 rate (20 h per half cycle). The voltage profile observed
was consistent with previous Si studies, with a long flat plateau
during the first charge, during which crystalline Si reacted with
Li to form amorphous LixSi. Subsequent discharge and charge
cycles had different voltage profiles characteristic of amorphous
Si (refs 24– 27). Significantly, the observed capacity during thisfirst charging operation was 4,277 mAh g21, which is essentiallyequivalent to the theoretical capacity within experimental error.
The first discharge capacity was 3,124 mAh g21, indicating a
coulombic efficiency of 73%. The second charge capacity
decreased by 17% to 3,541 mAh g21, although the second
discharge capacity increased slightly to 3,193 mAh g21, giving a
coulombic efficiency of 90%. Both charge and discharge

capacities remained nearly constant for subsequent cycles, withlittle fading up to 10 cycles (Fig. 2d), which is considerably better
than previously reported results8,9. As a comparison, our charge
and discharge data are shown along with the theoretical capacity(372 mAh g21) for the graphite currently used in lithium battery
anodes, and the charge data reported for thin films containing
12-nm Si nanocrystals8 (NCs) in Fig. 2d. This improved capacity
and cycle life in the Si NWs demonstrates the advantages of our
Si NW anode design.
The Si NWs also displayed high capacities at higher currents.
Figure 2c shows the charge and discharge curves observed at the
C/20, C/10, C/5, C/2 and 1C rates. Even at the 1C rate, thecapacities remained .2,100 mAh g21, which is still five times
larger than that of graphite. The cyclability of the Si NWs at thefaster rates was also excellent. Using the C/5 rate, the capacity
was stable at  3,500 mAh g21 for 20 cycles in another device(see Supplementary Information, Fig. S3). Despite the improved
performance, the Si NW anode showed an irreversible capacity
loss in the first cycle, which has been observed in other work5.
Although solid electrolyte interphase (SEI) formation has been
observed in Si (ref. 28), we do not believe this is the cause of ourinitial irreversible capacity loss, because there is no appreciablecapacity in the voltage range of the SEI layer formation(0.5 –0.7 V) during the first charge (Fig. 2b)8. Although SEI
formation may be occurring, the capacity involved in SEI
formation would be very small compared to the high charge
capacity we observed. The mechanism of the initial irreversible
capacity is not yet understood and requires further investigation.
The structural morphology changes during Li insertion werestudied to understand the high capacity and good cyclability of
our Si NW electrodes. Pristine, unreacted Si NWs were crystalline

32

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Si

Ni

Si
Ni

Number of nanowires

200
Initial
10 m V
100

0
0

100

200
Diameter (nm)8
Current (nA)

250 nmCurrent (µA)

20

50 nm

300

10
0
–10

4
0
–4

–20
–0.4

0.0
0.4
Voltage (V)

–0.4

0.0
0.4
Voltage (V)Figure 3 Morphology and electronic changes in Si NWs from reaction with Li. a,b, SEM image of pristine Si NWs before (a) and after (b) electrochemical cycling(same magnification). The inset in a is a cross-sectional image showing that the NWs are directly contacting the stainless steel current collector. c,d, TEM image of apristine Si NW with a partial Ni coating before (c) and after (d) Li cycling. e, Size distribution of NWs before and after charging to 10 mV (bin width 10 nm).
The average diameter of the NWs increased from 89 to 141 nm after lithiation. f, I – V curve for a single NW device (SEM image, inset) constructed from a pristine
Si NW. g, I – V curve for a single NW device (SEM image, inset), constructed from a NW that had been charged and discharged once at the C/20 rate.

with smooth sidewalls (Fig. 3a) and had an average diameter of
89 nm (s.d., 45 nm) (Fig. 3e). Cross-sectional scanning electron
microscopy (SEM) showed that the Si NWs grew off the substrateand had good contact with the stainless steel current collector(Fig. 3a, inset). After charging with Li, the Si NWs had roughly
textured sidewalls (Fig. 3b), and the average diameter increasedto 141 nm (s.d., 64 nm). Despite the large volume change, the
Si NWs remained intact and did not break into smaller particles.
They also appeared to remain in contact with the current
collector, suggesting minimal capacity fade due to electricallydisconnected material during cycling.
The Si NWs may also change their length during the change involume. To evaluate this, 25-nm Ni was evaporated onto as-grown
Si NWs using electron beam evaporation. Because of the shadow
effect of the Si NWs, the Ni only covered part of the NW surface(Fig. 3c), as confirmed by energy dispersed X-ray spectroscopy(EDS) mapping (see Supplementary Information, Fig. S4). The
Ni is inert to Li and acts as a rigid backbone on the Si NWs.
After lithiation (Fig. 3d), the Si NWs changed shape andwrapped around the Ni backbone in a three-dimensionally helicalmanner. This appeared to be due to an expansion in the lengthof the NW, which caused strain because the NW was attached to
the Ni and could not freely expand but rather buckled into ahelical shape. Although the NW length increased after lithiation,
the NWs remained continuous and without fractures,
maintaining a pathway for electrons all the way from thecollector to the NW tips. With both a diameter and length
increase, the Si NW volume change after Li insertion appears to
be about 400%, consistent with the literature5.
Efficient electron transport from the current collector to the Si
NWs is necessary for good battery cycling. To evaluate this, we
conducted electron transport measurements on single Si NWs
before and after lithiation (see Methods). The current versus
voltage curve on a pristine Si NW was linear, with a 25 kV
resistance (resistivity of 0.02 V-cm) (Fig. 3f ). After one cycle, theNWs became amorphous, but still exhibited a current that was
linear with voltage with an 8 MV resistance (resistivity of
3 V-cm) (Fig. 3g). The good conductivity of pristine and cycled
NWs ensures efficient electron transport for charge and discharge.
The large volume increase in the Si NWs is driven by thedramatic atomic structure change during lithiation. To
understand the structural evolution of NWs, we characterized the
NW electrodes at different charging potentials. The X-ray
diffraction (XRD) patterns were taken for initial pristine Si NWs,
Si NWs charged to 150 mV, 100 mV, 50 mV and 10 mV, as well as
after 5 cycles (Fig. 4a). XRD patterns of the as-grown Si NWs

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33© 2008 Nature Publishing GroupLETTERS
α-FeSi2 (001)Au(111)

From Si
From SSSi (111)(111)

From Au ( Li15Au4)
From α-FeSi2(220)
InitialCrystalAmorphous

150 mV
Intensity (a.u.)·112Ò

Crystal

100 mV
Crystal
50 mV
50 nm

100 nmAmorphous

50 nm

10 mV
CrystalAfter 5 cycles
3.3 Å
20

40

60
2θ (deg)

80

100

2 nm

Amorphous

CrystalAmorphous

Amorphous

3.3 Å
2 nm

5 nm

40 nm

Figure 4 Structural evolution of Si NWs during lithiation. a, XRD patterns of Si NWs before electrochemical cycling (initial), at different potentials during the first charge,
and after five cycles. b–e, TEM data for Si NWs at different stages of the first charge. b, A single-crystalline, pristine Si NW before electrochemical cycling. The SAED spots(inset) and HRTEM lattice fringes (bottom) are from the Si 1/3(224) planes. c, NW charged to 100 mV showing a Si crystalline core and the beginning of the formation of aLix Si amorphous shell. The HREM (bottom) shows an enlarged view of the region inside the box. d, Dark-field image of a NW charged to 50 mV showing an amorphous Lix Si
wire with crystalline Si grains (bright regions) in the core. The spotty rings in the SAED (inset) are from crystalline Si. The HRTEM (bottom) shows some Si crystal grains
embedded in the amorphous wire. e, A NW charged to 10 mV is completely amorphous Li4.4Si. The SAED (top) shows diffuse rings characteristic of an amorphous material.

showed diffraction peaks associated with Si, a-FeSi2, Au (the Si NW
catalyst) and stainless steel (SS). The a-FeSi2 forms at the interface
between the SS and the Si wires during the high temperature (5308C) NW growth process. The a-FeSi2 was not found to appreciably
react with Li during electrochemical cycling, although a small
amount of reaction has been reported24. After Si NWs werecharged to 150 mV, the higher angle Si peaks disappeared. Only
the Si(111) peak was still visible, but its intensity was greatly
decreased. This is consistent with the disappearance of theinitial crystalline Si and the start of the formation of amorphous
LixSi. The four broad peaks that appeared in the lower angles
are due to the formation of Li15Au4 (see Supplementary
Information, Fig. S5). At 100 mV, the pure Au peaks
disappeared, indicating that the Au had completely reacted with
Li. The Si(111) peak was very weak at 100 mV, anddisappeared completely at 50 mV. It appears that Si NWs
remain amorphous after the first charge, consistent with thenon-flat voltage charging/discharging curve in Fig. 2b. This
contrasts, however, with other studies on Si electrodes25,26, whichhave reported the formation of crystalline, Li3.75Si at potentials
less than 30 –60 mV. In situ XRD studies have determinedthat this crystalline phase only forms at ,50 mV for films
thicker than 2 mm (ref. 27). We did not observe this to be
the case in our Si NWs, most likely because of their shapeand small dimensions.
The local structural features of Si NWs during the first Li
insertion were studied with transmission electron microscopy(TEM) and selected area electron diffraction (SAED). The asgrown Si NWs were found to be single-crystalline. Figure 4b
shows an example of a typical Si NW with a k112l growth
direction29. Figure 4c shows a Si NW with a k112l growth
direction that was charged to 100 mV. In this case there were twophases present, as expected from the voltage profile. Bothcrystalline and amorphous phases were clearly seen. The
distribution of the two phases was observed both across thediameter (a crystalline core and an amorphous shell) and along
the length. The SAED showed the spot pattern for the crystalline
phase (Si), but weak diffuse rings from the amorphous phase
34(LixSi alloy) were also observed. Li ions must diffuse radially into
the NW from the electrolyte, resulting in the core– shell phase
distribution. The reason for phase distribution along the length is
not yet understood. At 50 mV, the Si NW became mostly
amorphous with some crystalline Si regions embedded inside thecore, as seen from the dark-field image and HRTEM (Fig. 4d).
The SAED showed spotty rings representative of a polycrystalline
sample and diffuse rings for the amorphous phase. At 10 mV(Fig. 4e), all of the Si had changed to amorphous Li4.4Si, as
indicated by the amorphous rings in the SAED. These TEM
observations were consistent with the XRD results (Fig. 4a) andvoltage charging curves (Fig. 2b).

METHODSSi NWs were synthesized using the VLS process on stainless steel substrates using
Au catalyst. The electrochemical properties were evaluated under an argon
atmosphere by both cyclic voltammetry and galvanostatic cycling in a threeelectrode configuration, with the Si NWs on the stainless steel substrate as theworking electrode and Li foil as both reference and counter-electrodes. No
binders or conducting carbon were used. The charge capacity referred to here is
the total charge inserted into the Si NW, per mass unit, during Li insertion,
whereas the discharge capacity is the total charge removed during Li extraction.
For electrical characterization, single Si NW devices were contacted with metalelectrodes by electron-beam lithography or focused-ion beam deposition. For
more detailed descriptions of NW synthesis, TEM and XRD characterization,
electrochemical testing, and device fabrication, see the Supplementary
Information.

Received 23 July 2007; accepted 14 November 2007; published 16 December 2007.
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Acknowledgements
We thank Dr Marshall for help with TEM interpretation and Professors Brongersma and Clemens fortechnical help. Y.C. acknowledges support from the Stanford New Faculty Startup Fund and Global
Climate and Energy Projects. C.K.C. acknowledges support from a National Science Foundation Graduate
Fellowship and Stanford Graduate Fellowship.
Correspondence and requests for materials should be addressed to Y.C.
Supplementary information accompanies this paper on www.nature.com/naturenanotechnology.

Author contributions
C.K.C. conceived and carried out the experiment and data analysis. H.P., G.L., K.M. and X.F.Z. assisted inexperimental work. R.A.H. carried out data analysis. Y.C. conceived the experiment and carried out data
analysis. C.K.C., R.A.H. and Y.C. wrote the paper.
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