In this study, EBIC technique was applied successfully to observe the growth of
defects inside silicon MEMS structures. The changes of local contrast were successfully observed at the notch tip of the specimens, which remained the same through the hydrofluoric
acid treatment after the experiment. The damage, which caused the local contrast changes,
was not the thickened surface oxide layer but the evolution of intrinsic defects being likely
dislocations inside the crystal of silicon. These are the first direct evidences of fatigue
mechanism in silicon. However, the resolution of the obtained EBIC pictures in this study
is not high enough to estimate the structure of damage. To further elucidate the fatigue
mechanism in silicon MEMS structures, experiment with EBIC observation is necessary
to be improved to obtain the pictures at atomistic scale by using EBIC technique with
high resolution SEM or STEM.
12 trang |
Chia sẻ: huongthu9 | Lượt xem: 458 | Lượt tải: 0
Bạn đang xem nội dung tài liệu A direct evidence of fatigue damage growth inside silicon mems structures obtained with ebic technique, để tải tài liệu về máy bạn click vào nút DOWNLOAD ở trên
Volume 36 Number 2
2
2014
Vietnam Journal of Mechanics, VAST, Vol. 36, No. 2 (2014), pp. 109 – 118
A DIRECT EVIDENCE OF FATIGUE DAMAGE
GROWTH INSIDE SILICON MEMS STRUCTURES
OBTAINED WITH EBIC TECHNIQUE
Vu Le Huy1,∗, Shoji Kamiya2
1Hanoi University of Science and Technology, Vietnam
2Nagoya Institute of Technology, Japan
∗E-mail: huy.vule@hust.edu.vn
Received October 16, 2013
Abstract. Electron beam induced current (EBIC) is a semiconductor analysis technique
performed in a scanning electron microscope (SEM) or scanning transmission electron
microscope (STEM). It is able to sense defects beneath the surface even invisible by
SEM. This paper presents the results of a trial to observe the defect growth inside silicon
MEMS structures under fatigue loading by applying EBIC technique. The tests were
performed on two specimens fabricated from an n-type single crystal silicon wafer. While
the test region of the specimens was repeatedly subjected to compressive stress, EBIC
images were obtained to visualize damage evolution which presented by the growth of the
dark region on EBIC images. It was proved that the damage is not due to the growth of
oxidation layer on the surface of the specimens but due to the growth of intrinsic defects
of silicon crystal. The results would be evidences to elucidate that the fatigue damages
grow inside silicon MEMS structures but not in oxidation layer.
Keywords : EBIC, silicon, MEMS, defect, fatigue, dislocation.
1. INTRODUCTION
Microelectromechanical systems (MEMS) are devices with highly miniaturized me-
chanical components fabricated using batch processing techniques inspired by integrated
circuit (IC) technologies, which have been among the fastest growing technologies, open-
ing new frontiers of microtechnology [1, 2]. They have already been applied to various
fields such as medical treatment and aerospace equipment where the reliability of MEMS
structures is of serious concern. The mechanical reliability of MEMS has recently been
attracting more and more interest.
Silicon is the most common structural material for MEMS. Since the end of the
last century, many evidences have been found that they are susceptible to fatigue, which
is the weakening of a material caused by repeatedly applied loads. Up to now, fatigue
mechanism of micro-scale silicon structures is still under the debate. The most commonly
accepted model of fatigue process has been the reaction layer model [3, 4], where the
surface oxide layer is thickened with cyclic stress and subjected to corrosion cracking.
110 Vu Le Huy, Shoji Kamiya
However, this theory could not explain for the case of low-cycle fatigue [5, 6], where the
time was not enough for oxygen to diffuse into silicon. In contrast, however, it was also
claimed that the thickening of a surface oxide layer due to cyclic stress was not observed
until fatigue fracture on polysilicon devices with 3 nm thin native oxide [7] showing a
counter evidence against the reaction layer model. Another mechanism was proposed that
subcritical crack growth in silicon itself assisted through wedging of asperities on the crack
surfaces [8, 9]. On the other hand, recent indirect evidences from the researches in Japan
[10, 11] suggested another possibility of fatigue mechanism on the basis of dislocation
mobility. For example, steps approximately 5 nm in height indicating dislocation slip lines
were observed on the surface of 200 nm wide doubly supported beams made of single
crystal silicon when bent with an atomic force microscope at 373 K [12]. Ductile behavior
of nano-scale silicon at room temperature was also observed in other studies [13–15]. The
fracture toughness of single crystal silicon films with 4 µm thickness was also reported to
sharply increase above 70◦C from 1.3 to 2.5 MPam1/2 [16]. In other words, the increase
of fracture toughness of single crystal silicon films at room temperature corresponds to
the decrease of specimen thickness. This suggested that the increase in the dislocation
mobility is related to the thickness reduction [11]. Dislocations emitted from the fracture
surface created at room temperature in 1-µm-thick specimen were also directly observed
with a transmission electron microscope [11]. The current understanding about the fatigue
behaviors of silicon up to now is from the accumulation of experimental results and the
observations on specimens after fatigue tests. Therefore, direct evidences to elucidate the
fatigue mechanism of silicon structures in MEMS are necessary.
Electron beam induced current (EBIC) is known to be a semiconductor analysis
technique performed in a scanning electron microscope (SEM) or scanning transmission
electron microscope (STEM) [17]. It can be used to identify buried junctions or defects in
semiconductors, or to examine minority carrier properties. It measures the current gen-
erated by the electron beam through a junction potential, which is able to sense defects
beneath the surface even invisible by SEM. In this paper, EBIC technique is applied to see
whether the defects eventually grow inside silicon under fatigue loading corresponding to
the equivalent crack extension as modeled in our previous study [18]. Since it is expected
that compressive stress accumulates the damage more efficiently [19], the observation in
this study is performed with single crystalline silicon specimen tested with cyclic compres-
sive stress. EBIC pictures should give direct evidences to elucidate fatigue mechanism of
silicon MEMS structures.
2. EBIC TECHNIQUE
EBIC technique is based on the two schemes of setup as shown in Fig. 1 for the
cases of plan-view and cross-section-identification. Plan view means that the p-n junction is
perpendicular to the electron beam, whereas in cross-section-identification the p-n junction
is parallel to the SEM beam. When an electron beam strikes a semiconductor sample, it
will generate electron-hole pairs in an interaction volume. If they are near the p-n junction,
they will diffuse to the junction. Electrons and holes will be drift to the n- type and p+
type, respectively. When the p+ and n- types are connected to a picoammeter or current
A direct evidence of fatigue damage growth inside silicon MEMS structures obtained with EBIC technique 111
Fig. 1. Schemes of EBIC observation for (a) plan-view and (b) cross-section-identification
amplifier, they will produce an EBIC. This current can be used as the imaging signal
for SEM or STEM. By connecting the EBIC signal scanned on observation region, EBIC
image is obtained. For the case of plan-view, defects such as dislocations tend to strongly
decrease the minority carrier in their vicinity, so the EBIC signal is strong in areas without
the defects and weak in areas around the defects. Therefore, it should figure out the defects
in silicon in terms of contrast change on its image.
3. SPECIMEN AND EXPERIMENTAL SETUP
3.1. Specimen
Fig. 2 shows the design of specimen used in EBIC observation experiment. The
unit of dimensions is mm. The length and the thickness of the specimen are 18 mm and
0.38 mm, respectively. It was designed with a small test section in the upper part as a
horizontal beam which is supported at both the ends by the two vertical arms connected
to the base plate in the lower part. The length of the horizontal beam is 4 mm. Specimens
were fabricated as schematically illustrated in Fig. 3 out of a n- type single crystal silicon
wafer (thickness 380 µm, dopant Sb, conductivity 0.1 Ωcm) by applying a deep reactive
ion etching (DRIE) process starting from the top surface of the wafer. The etched side
surface has an inclination of 3 degrees, because of the characteristics of DRIE. Therefore,
Fig. 2. Specimen used for EBIC observation
112 Vu Le Huy, Shoji Kamiya
Fig. 3. Schematic illustration of fabrication process for the specimens
the heights of the cross section on the top and bottom surfaces of the wafer are 0.25 mm
and 0.21 mm, respectively.
Boron was ion-implanted on the upper etched surface of the test section to compose
a p+ layer, with the accelerating voltage of 5 kV and dosage of 1.0×1015 cm−2. The
junction underneath the p+ layer was utilized for the EBIC observation to explore the
damage. For an ohmic contact to the n- type area, Au-0.5%Sb was deposited on the lower
part of the specimen. The specimen was then annealed for 5 minutes in nitrogen at 900◦C
for the activation of dopants. Finally, two notches with 15 µm tip radius were created
with a dicing saw, which were tilted by +45 and -45 degrees to the surface. The distance
between the two notches was designed as 0.01 mm.
3.2. Experimental setup
Fig. 4 shows the experimental setup for EBIC observation of the specimen tested
with cyclic loading. An environmental scanning electron microscope (ESEM) shown in
Fig. 4(a) was used to perform EBIC observation. Specimen was kept by a state mounted
on the holder inside the chamber of the ESEM as shown in Fig. 4(b). A piezo-positioner
actuator (PI P-841.20, travel: 30 µm, resolution: 0.6 nm) was used to drive the setup as in
Fig. 4(c). The applied load was measured by a load-cell LUR-A-100NSA1 manufactured by
Kyowa Electronic Instruments Co., LTD. with a rated capacity 100 N. They were controlled
by the equipments such as the computer, the function generator, etc., and monitored by the
oscilloscope from outside of the chamber as shown in Fig. 4(a). The horizontal actuation
given by the actuator was converted into the vertical stroke of loading rod indenters via
A direct evidence of fatigue damage growth inside silicon MEMS structures obtained with EBIC technique 113
Fig. 4. Experimental setup for fatigue test in ESEM
an elastic torsion spring indicated in Fig. 4(c). These rod indenters pushed downward
the upper surface of the test section at the two points indicated in Fig. 2 because of the
inclination of the etched surface. The specimen was fixed to stand up vertically as shown
in Fig. 4(d). By this way, the upper etched surface of the test section (indicated by EBIC
observation region in Fig. 2) was facing to the electron beam while being subjected to a
compressive stress. The EBIC cables shown in Fig. 4(d) are connected to the specimen
and SEM display as illustrated in Fig. 2.
3.3. Evaluation of applied stress
The stress distribution on the EBIC observation region was analyzed by the finite
element method (FEM) with ANSYS 14.0 software. In design, maximum compressive stress
on the EBIC observation region was 75.6MPa when the load applied to the specimen was
1N. The distance between the two notches was expected to be 0.01mm, but it was not
able to be fabricated exactly. Therefore, FE analysis was performed individually for each
specimen with the actual size of notches measured after creating the notches in order to
obtain the exact value of the applied stress. Fig. 5 shows the stress distribution on the
EBIC observation region of a specimen tested in this study. In this model, applied load
was 20N, and thus the maximum compressive stress is 1.57GPa. The results obtained
from FEM were used to calculate the maximum stress on the observation region when the
load applied to specimen in the tests was known.
114 Vu Le Huy, Shoji Kamiya
Fig. 5. Experimental setup for fatigue test in ESEM
4. RESULTS AND DISCUSSION
In this study, two specimens were tested by applying the cyclic loading with fre-
quency of 50 Hz. The fatigue tests were occasionally interrupted to obtain EBIC images
with an acceleration voltage of 30 kV as shown in Figs. 6 and 7. The properties and
implemented conditions of these specimens are summarized in Tab. 1.
Table 1. Summarization of the specimens
Specimen number #1 #2
Measured distance between the two notches
(µm)
27 18
Gas pressure (Pa) inside ESEM chamber during
fatigue test
560 40
Relative humidity (%) 20 4
Gas pressure (Pa) inside ESEM chamber when
taking EBIC pictures
40 40
Applied maximum compressive stress (GPa) 0.89 0.82
Total number of cycles in fatigue test 2×105 cycles 5×105 cycles
Results of EBIC observation Fig. 6(c) Fig.7
For the first specimen (specimen #1), fatigue test was performed in the environment
with gas pressure of 560 Pa which corresponds to 20% of relative humidity. Its SEM picture
before the fatigue tests is shown in Fig. 6(a). Firstly, the maximum compressive stress
applied to the EBIC observation region of the specimen was 0.62 GPa. EBIC pictures
shown in Fig. 6(b) were taken during this test at gas pressure inside the ESEM chamber
of 80 Pa. There was no noticeable change in the EBIC pictures from before the fatigue
test (0 cycles) to after 5×105 cycles as shown in Fig. 6(b). This is consistent with the
A direct evidence of fatigue damage growth inside silicon MEMS structures obtained with EBIC technique 115
SEM
(a)
10 mm
0 cycles 5´10 52 cycles 5 cycles´10
(b)
10 mm
52 cycles´100 cycles 5cycles10
(c)
10 mm
SEM EBIC
(d)
Fig. 6. Observation results of Specimen #1 with (a) SEM picture before the test,
(b,c) EBIC pictures the during fatigue loading process when the applied compressive
stress was (b) 0.62 GPa and (c) 0.89 GPa, and (d) after HF treatment
previous trial where the same stress level was applied to specimen but it was not able to
see any clear change [20]. By increasing the maximum compressive stress to 0.89 GPa, the
EBIC pictures were obtained as shown in Fig. 6(c). These EBIC pictures were taken at
gas pressure inside the ESEM chamber of 40 Pa. The change in the EBIC pictures was
clearly observed. The dark region was seen to expand as the cycle number of applied load
increases. After these fatigue tests, the specimen was etched by using 10%HF solution
in 10 minutes, whose etch rate against thermal oxide is estimated to be 23 nm/min [21].
Therefore it should remove whole the silicon oxide layer, even if it would be so thick as 100
nm as presented in the other reports [4], locally exists at areas with stress concentration.
If there would have been a locally grown silicon oxide layer on the surface to reduce
EBIC, the image after HF treatment should have returned to the original image before
fatigue loading. Fig. 6(d) shows the SEM and EBIC pictures of this specimen after etching.
There was no marked difference between the EBIC images before and after HF treatment.
Therefore, the changes in EBIC images were not due to the growth of surface oxide layer
but growth of defects inside silicon.
116 Vu Le Huy, Shoji Kamiya
10 mm
SEM
10 mm
0 cycles 5´10 52 cycles 5 cycles´10
Fig. 7. Observation results of Specimen #2 when the applied compressive stress was 0.82 GPa
For the second specimen (specimen #2), fatigue test was performed in the envi-
ronment with gas pressure of 40 Pa. The maximum compressive stress was 0.82 GPa. Its
SEM and EBIC pictures were obtained as shown in Fig. 7. Gas pressure when taking
those pictures was 40 Pa. The change in the EBIC pictures was also observed as the dark
region gradually widening with the increment of number of cycles. With gas pressure of
40 Pa in this fatigue test corresponded to 4% of relative humidity, the effect of oxidation
is negligible, and therefore HF treatment is not necessary for this specimen. On the other
hand, the results show that the velocity of the dark region growth on the specimen #2
was slower than that of the specimen #1 due to the lower level of applied stress. It means
that the expansion of the dark region presents an accumulation process of recombination
defects generated in crystal during fatigue loading, which reduced the EBIC signal.
5. CONCLUSION
In this study, EBIC technique was applied successfully to observe the growth of
defects inside silicon MEMS structures. The changes of local contrast were successfully ob-
served at the notch tip of the specimens, which remained the same through the hydrofluoric
acid treatment after the experiment. The damage, which caused the local contrast changes,
was not the thickened surface oxide layer but the evolution of intrinsic defects being likely
dislocations inside the crystal of silicon. These are the first direct evidences of fatigue
mechanism in silicon. However, the resolution of the obtained EBIC pictures in this study
is not high enough to estimate the structure of damage. To further elucidate the fatigue
mechanism in silicon MEMS structures, experiment with EBIC observation is necessary
to be improved to obtain the pictures at atomistic scale by using EBIC technique with
high resolution SEM or STEM.
REFERENCES
[1] H. Fujita. Microactuators and micromachines. In Proceedings of the IEEE, Vol. 86.
IEEE, (1998), pp. 1721–1732.
[2] M. J. Madou. Fundamentals of microfabrication: The science of miniaturization. CRC
press, (2002).
[3] C. L. Muhlstein, S. B. Brown, and R. O. Ritchie. High-cycle fatigue of single-crystal
silicon thin films. Journal of Microelectromechanical Systems, 10, (4), (2001), pp. 593–
600.
REFERENCES 117
[4] C. Muhlstein, E. Stach, and R. Ritchie. A reaction-layer mechanism for the delayed
failure of micron-scale polycrystalline silicon structural films subjected to high-cycle
fatigue loading. Acta Materialia, 50, (14), (2002), pp. 3579–3595.
[5] E. Baumert, P.-O. Theillet, and O. Pierron. Investigation of the low-cycle fatigue
mechanism for micron-scale monocrystalline silicon films. Acta Materialia, 58, (8),
(2010), pp. 2854–2863.
[6] P.-O. Theillet and O. Pierron. Fatigue rates of monocrystalline silicon thin films in
harsh environments: Influence of stress amplitude, relative humidity, and temperature.
Applied Physics Letters, 94, (18), (2009), pp. 181915–181915.
[7] H. Kahn, A. Avishai, R. Ballarini, and A. Heuer. Surface oxide effects on failure of
polysilicon MEMS after cyclic and monotonic loading. Scripta Materialia, 59, (9),
(2008), pp. 912–915.
[8] H. Kahn, R. Ballarini, J. Bellante, and A. Heuer. Fatigue failure in polysilicon not
due to simple stress corrosion cracking. Science, 298, (5596), (2002), pp. 1215–1218.
[9] H. Kahn, R. Ballarini, and A. Heuer. Dynamic fatigue of silicon. Current Opinion in
Solid State and Materials Science, 8, (1), (2004), pp. 71–76.
[10] N. Kato, A. Nishikawa, and H. Saka. Dislocations in Si generated by fatigue at room
temperature. Materials Science in Semiconductor Processing, 4, (1), (2001), pp. 113–
115.
[11] S. Nakao, T. Ando, S. Arai, N. Saito, and K. Sato. Variation in dislocation pattern
observed in SCS films fractured by tensile test: Effects of film thickness and testing
temperature. In MRS Proceedings, Vol. 1052. Cambridge Univ Press, (2007).
[12] T. Namazu, Y. Isono, and T. Tanaka. Plastic deformation of nanometric single crystal
silicon wire in AFM bending test at intermediate temperatures. Journal of Micro-
electromechanical Systems, 11, (2), (2002), pp. 125–135.
[13] X. Han, K. Zheng, Y. Zhang, X. Zhang, Z. Zhang, and Z. L. Wang. Low-temperature in
situ large-strain plasticity of silicon nanowires. Advanced Materials, 19, (16), (2007),
pp. 2112–2118.
[14] F. O¨stlund, K. Rzepiejewska-Malyska, K. Leifer, L. M. Hale, Y. Tang, R. Ballarini,
W. W. Gerberich, and J. Michler. Brittle-to-ductile transition in uniaxial compression
of silicon pillars at room temperature. Advanced Functional Materials, 19, (15),
(2009), pp. 2439–2444.
[15] J. Nowak, A. Beaber, O. Ugurlu, S. Girshick, and W. Gerberich. Small size strength
dependence on dislocation nucleation. Scripta Materialia, 62, (11), (2010), pp. 819–
822.
[16] S. Nakao, T. Ando, M. Shikida, and K. Sato. Effect of temperature on fracture
toughness in a single-crystal-silicon film and transition in its fracture mode. Journal
of Micromechanics and Microengineering, 18, (1), (2008), p. 015026.
[17] C. Parish, D. Batchelor, C. Progl, and P. Russell. Tutorial: Electron beam-induced
current in the scanning electron microscope. Microscopy and Analysis, 21, (2007),
pp. 11–13.
[18] V. L. Huy, J. Gaspar, O. Paul, and S. Kamiya. Statistical characterization of fatigue
lifetime of polysilicon thin films. Sensors and Actuators A: Physical, 179, (2012),
pp. 251–262.
118 REFERENCES
[19] K. Shima, S. Izumi, and S. Sakai. Reaction pathway analysis for dislocation nucleation
from a sharp corner in silicon: Glide set versus shuffle set. Journal of Applied Physics,
108, (6), (2010), DOI: 10.1063/1.3486465.
[20] S. Kamiya, R. Hirai, H. Izumi, N. Umehara, and T. Tokoroyama. Direct observation
of damage accumulation process inside silicon under mechanical fatigue loading. In
Proceedings of the 17th International Conference on Solid-State Sensors, Actuators
and Microsystems, Transducers & Eurosensors XXVII, (2013), pp. 784–787.
[21] K. R. Williams, K. Gupta, and M. Wasilik. Etch rates for micromachining processing-
part II. Journal of Microelectromechanical Systems, 12, (6), (2003), pp. 761–778.
VIETNAM ACADEMY OF SCIENCE AND TECHNOLOGY
VIETNAM JOURNAL OF MECHANICS VOLUME 36, N. 2, 2014
CONTENTS
Pages
1. Dao Huy Bich, Nguyen Dang Bich, A coupling successive approximation
method for solving Duffing equation and its application. 77
2. Nguyen Thai Chung, Hoang Xuan Luong, Nguyen Thi Thanh Xuan, Dynamic
stability analysis of laminated composite plate with piezoelectric layers. 95
3. Vu Le Huy, Shoji Kamiya, A direct evidence of fatigue damage growth inside
silicon MEMS structures obtained with EBIC technique. 109
4. Nguyen Tien Khiem, Duong The Hung, Vu Thi An Ninh, Multiple crack
identification in stepped beam by measurements of natural frequencies. 119
5. Nguyen Hong Son, Hoang Thi Bich Ngoc, Dinh Van Phong, Nguyen Manh
Hung, Experiments and numerical calculation to determine aerodynamic char-
acteristics of flows around 3D wings. 133
6. Gulshan Taj M. N. A., Anupam Chakrabarti, Mohammad Talha, Free vi-
bration analysis of four parameter functionally graded plate accounting for
realistic transverse shear mode. 145
Các file đính kèm theo tài liệu này:
- a_direct_evidence_of_fatigue_damage_growth_inside_silicon_me.pdf