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Chapter 1
Introduction
1-1 General Background
Since 1960, chip functions can be improved by scaling down the
volumes of the transistors and enhancing abilities of computing. Basically
the progression of IC follows the Moore’s law, the roadmap by Intel is
shown at Figure 1-1. But in the future, due to lithography and physical
limitation, the development of scaling down will meet its bottleneck [1].
Not only the transistor itself gets the limitation but also the number of
transistors keeps increasing on the single chip. The key to dominate IC
performance is not the single transistor anymore. The global interconnect
RC delay plays an important role [2]. Although it can reduce the
transmission distance of some important areas by IC design, the total
conduct distances are still the same. If the chip function needs to keep
making progressing, efficiently reducing the total transmission distance
of conduce lines is the essential factor.
Moreover, semiconductor industries always increase some unique
processes and materials with requests of boosting IC function. So the
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heterogeneous integration is more important than usual, this concept is
described at Figure 1-2. This kind of heterogeneous integration involves
using different heterogeneous substrate materials and fabricating chips at
different process temperatures. For integration of heterogeneous substrate
materials, it is apparently to use new approaches to integrate them
together. And for fabricating chips at different process temperatures, the
latter process temperature needs to lower than the former one. Or it will
exceed the thermal budget; this will restrict many transistors application
like the waveguide transistors and the integration of traditional CMOS
[3].
For the purpose of resolving the challenges and requirement above,
the concepts of 3D Integration and 3D IC appear. The general idea of 3D
IC technique is to change the traditional method placing IC at X and Y
two dimensions. It enhances Z dimensions. The space of vertical stacking
can be created. According to this concept, utilizing 3D technique can
avoid the problems of traditional 2D IC keeping scaling down like the too
long total conduct lines and the volume of chips is too large to get the
frivolous requirements in Figure 1-3 [4].
3D IC technique always uses two methods which are wafer bonding
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and chip stacking. And it use through–silicon via (TSV) to connect the
thinning wafers and chips. It can convert the traditional 2D IC to 3D IC,
and the benefits are shown in Figure 1-4.
Due to 3D IC can efficiently put the space to use and shorten the
transmission distance of current signals, resistance-capacitance delay and
total resistance can be reduced. Besides, owing to using these unique
concepts of wafer bonding and chip stacking, fabrications of
heterogeneous substrate materials can be separated at the beginning and
stack together in the end. As mentioned above, the process temperatures
and other circumstance requirements will restrict different ICs. But now
these problems can be resolved by the method of stacking. Through
optimized design of the chip stacking, the heterogeneous integration of
3D-IC can achieve future demand. Form SoC to SiP, 3D SiP and
Terminal product 3D-IC as shown in Figure1-5. And TSV technology can
provide more benefits which is shown as Figure 1-6. So 3D IC can
provide a lot of advantages like multi-functions heterogeneous integration,
high performance and low power dissipation under the requirements of
frivolous demands and cost down.
Due to this characteristic concept of 3D IC, this technology will
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subvert traditional 2D IC. And it is closely linked to IC design, process
techniques, instruments, packaging, testing methods, terminal product
application and performance. These fields will dominate the maturity of
3D IC and its terminal products. In other words, 3D IC is a novel
technology to integrate all fields. In all these fields, the process of 3D IC
is the most essential factor [5].
3D IC brings many new process techniques such as wafer bonding,
chip stacking, TSV fabrication and wafer thinning in Table I-I. Directions
of stacking are face-to-face and face-to-back. And stacking approaches
are die-to-die, die-to-wafer and wafer-to-wafer. In addition, 3D IC
involves using different substrate materials, bonding materials and
stuffing materials. So many derivative phenomena of material and
physics need to be resolved. Under so many kinds of process selections,
developing 3D IC with low cost, high yield and high performance is the
most key point.
1-2 Motivation – Why do we need good oxide bonding quality and
ultra-thin Si layer transfer?
Bonding in 3D IC is an important region, the application of bonding
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can be used on heterogeneous integration, reduce RC delay, small form
factor, high performance, high throughput, low power consumption,
hetero-integration and so on. It is the key of 3D IC technology. There are
three major bonding methods which are metal-to-metal,
polymer-to-polymer and oxide-to-oxide. Metal bonding has some
advantages that other bonding techniques can’t achieve, such as it can be
served as an extra metal layer, good heat dissipation, strong bonding
strength, less cleanness requirement and it is softer than oxide. And also
there are some metals materials used for bonding have been researched
such as Cu, Ti, Sn, and Au [6-7]. These metals are often used in the
semiconductor industry. But it major weakness is contaminant issue, so it
can only use at BEOL (Back-End-Of-Line)
Polymer bonding can provide an opportunity to achieve a low
temperature in photo-sensitive patterned technique suitable for MEMS,
and 3D integration, packaging of VLSI for smaller size packaging. The
advantages include low bonding temperature about below 300℃, an
extremely high bonding strength, no metal ion contamination to device,
excellent surface planarization property, and high plasticity to absorb the
stress induced during bonding process. But such as above, polymer
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bonding also have contamination issue, and the process after bonding
can`t be too high or transubstantiation will occur, then bonding strength
will reduce and bring our reliability problem.
Oxide bonding can use at FEOL (front-end-of-line), compatible with
now days semiconductor procedure and can bonding at relative low
temperature. Semiconductor history keep following Moore`s Law so the
device are is getting smaller, some problems appear and will getting more
worse, such as leakage current, SCE (short channel effect), DIBL (drain
induce barrier lower) and so forth. If there is a silicon substrate that cover
ultra-thin silicon layer on oxide layer can reduce these problems which
affect device performance and improve electric characteristic, but the
main issue is that substrate source is too expensive compare to traditional
silicon wafer. Because it has so many advantages, so how to develop an
easy and fit in with economic concern is very important. The objectives
of this research are to development of ultra-thin bulk silicon wafer
thinning technology to improve the performance of the device on it.
Because it has so many applications in semiconductor procedure, our goal
is make backside illumination CMOS image sensor (BSI-CIS) on the
substrate that we mentioned before. BSI-CIS is the next generation image
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sensor, it has many advantages compare to front side illumination CMOS
image sensor (FSI-CIS), like reduce the noise signal beyond low
illumination to lighten color distortion, enhance the sensor current, lower
the effect of Young's interference so the sensor can further scaling and so
on. In this age, most of cell phone are integrated with camera, and the
evolution of cell phone is scaling beneath more function, under these
proposes, BSI-CIS is essential to study.
Because the whole process is too hard to accomplish directly, so our
goal is to accomplish the ultra-thin silicon substrate less than 4μm to
developing BSI-CIS testing structure and accomplishing optical-electrical
devices stacks with memory by 3D-IC bonding technology.
1-3 Organization of the Thesis
In Chapter 2, the major characteristics of all instruments which are
used in this thesis will be literally introduced. In Chapter 3, we do chip
level and wafer level oxide bonding parameter identification, procuring
solution, oxide species choice, bonding temperature, given force
magnitude, and given force type. In Chapter 4, develop procedure to do
ultra-thin Si transfer on oxide, analysis H atoms diffuse result, inspect
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transferred silicon film quality. In Chapter 6, it will jump to conclusion
for this thesis and make some suggestions. Also the future work for this
study will be told.
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(Intel)
Figure 1-1 Intel demonstrates roadmap
(Zycube, MNCN)
Figure 1-2 3D-IC technology integrate different function chips by
heterogeneous stack
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( LETI, EMC 2007)
Figure 1-3 3D integration can improve performance compare with now
days 2D circuit
(Sematech and Gartner)
Figure 1-4 Comparison between SoC, SiP, and 3D-IC
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(Yole development)
Figure 1-5 Development of 3D-IC scheme
(Yole development)
Figure 1-6 Comparison between wire bonding and TSV
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Category Detail terms
Stacking approaches
a. Die to Die (D2D)
b. Die to Wafer (D2W)
c. Wafer to Wafer (W2W)
Wafer selection a. Bulk (Si, Ge, GaAs, sapphire)
b. SOI
Bonding method
a. Metal to Metal
b. Oxide to Oxide
c. Polymer to Polymer
Direction of stacking a. Face to Face
b. Face to Back
Fabrication of TSV
a. Via first
b. Via middle
c. Via last
Table I-I Classification of 3D IC processes and integration techniques
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Chapter 2
Experimental Instruments
2-1 Introduction
In this chapter, some of the equipment instruments are been
described. They play an important role in our research. It is divided into
two parts to do introduction: process instruments and material analysis
instruments. All the samples studied in this work are prepared in Nano
Facility Center (NFC), Center for Nanotechnology, Materials Science,
and Microsystems (CNMSM) and National Nano Device Laboratories
(NDL). Material analysis and microscope instruments are used to let us
understand the related and the corresponding properties of the process
condition. Transmission Electron Microscopy (TEM), Secondary Ion
Mass Spectroscopy (SIMS), and scanning electron microscopy (SEM) are
used. All the instruments will be introduced as follows. Figure 2-1 will
summarize main flow of experimental procedures and material analyses.
2-2 Process Instruments
I. Oxford Plasma Enhanced Chemical Vapor Deposition system
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Plasma enhanced chemical vapor deposition (PECVD) is usually
used for the thin film deposition, and let material source change from gas
state into plasma state to accelerate chemical reactions, the outlook of
PECVD shows at Figure 2-2. The plasma is filled by process gases and
generated by two electrodes which is bias with RF signal or DC signal.
Processing plasmas are usually operated at the pressures of a few mTorr
to a few Torr so the atoms and ions can reach enough meant free path.
Ionized atoms or molecules are accelerated towards or leave the
neighboring surface in sheath region (depends on their charges); therefore,
all surfaces exposed to the plasma receive energetic ion bombardment.
The potential across the sheath layer is typically only 10–20 V, the sheath
layer is naturally generated because those electrons move faster than
atoms or molecules, and can produce much higher sheath potential by
modified reactor geometry. Ion bombardment is not only leaded to
increases in density of the film but also remove contaminants that cover
the sample surface to improving film quality. Ion bombardment density
can be high enough to do planarization of thin film. Silicon dioxide can
be deposited by using different silicon precursor gasses like
dichlorosilane or silane and oxygen precursors. Silicon nitride can be
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formed by using silane and nitrogen or ammonia. Silicon Dioxide can
also be deposited from a tetra-ethyl-ortho-silicate (TEOS) silicon
precursor in oxygen or oxygen-argon plasma. Silicon dioxide deposited
by High-density plasma can create a nearly hydrogen-free film with good
conformality.
II. Bonder
This multipurpose bonding platform FINEPLACER Pico MA for
advanced assembly can process bonding step where 5 μm accuracy shows
at Figure 2-3. And it has high magnification to do alignment procedure.
Advanced device packaging like assembly of MEMS, sensors, RFID,
embedded components and surface mount photonics can be completed at
this bonder. Also, it can execute precise die attach, flip chip bonding,
LED bonding and chip to wafer (6”) bonding. Some high technologies
have been adopted on this instrument such as thermo compression,
thermo sonic, ultrasonic bonding, soldering (AuSn, C4, Indium),
face-up/face-down assembly, flip chip on flex, chip on glass (CoG) and
adhesive technologies (ACF/ACP/NCP). Some features are spotlighted
like vision alignment system ensures placement accuracy 5μm, larger
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field of view and working area (6”), shifting module for bigger chip sizes,
quick and easy setup of new applications, manual & motorized
configuration available, hands-off operation in motorized configuration,
high resolution video optics with fiber optic lighting, process observation
and monitoring and independent substrate handling without tool change.
Its software “WinFlipChip” can advanced process recording and
reporting functions, control of all connected process modules, advanced
force control, drag & drop function to adjust profiles, options to capture
pictures and movies and graphical user interface. The outlook of
FINEPLACER Pico MA is shown in Figure 2-2.
III. Electronic Visions Co.501 (EV501)
EVG501 is a bonding tool that can achieve wafer level bonding
shows at Figure 2-4, it is compatible with double side aligner, and then
aligned wafer level bonding can be done. EVG501 supports a variety of
bonding processes, such as anodic, glass frit, eutectic, diffusion, fusion,
solder, and adhesive bonds, as well as other thermal processes, including
high temperature bakes under a controlled atmosphere. Bonding with
EVG501 don`t need adhesive glue, but heat two wafers and apply voltage
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to make them bonded. The theory of anodic bonding is that when heat
wafers to 300℃~ 400℃, the metal ions in glass will move and have
conductivity, if applied negative voltage at glass side, then metal ions will
attracted by electrode to glass surface, the trapped negative ions at glass
surface will form a electron layer with silicon surface nearby, it is thought
that this electron layer will form ionic bond between silicon dioxide and
silicon wafer, this bonding method often begin from the negative
electrode to whole wafer.
EVG501 only support 4 inch wafer process and it is a semi-automatic
machine that can heat or cool down upper and bottom wafers at the same
time in the process, besides, EVG501 can provide a vacuum bonding
environment to reach a better result.
IV. EVG520HE
The EVG520HE is a thermo-compress bonding tool shows at Figure
2-5; the theory of thermo-compress bonding is using pressure and heat to
make the contact area between these two wafers distortion slightly to
increase contact area. At a certain temperature that is high enough at the
wafer surface, these wafers will going diffuse between each other to make
- 18 -
the bonding process complete, but this method doesn`t require strict
surface cleaning and high vacuum condition.
Because thermo-compress bonding process is simpler and cost less,
it`s more attractive to industry and academic circle, more effort,
investigation and development are put in. The most important parameter
in this method is temperature cause wafer level bonding is used at 3D-IC
electron device and application, so the bonding temperature should
compatible with BEOL (back-end-of-line) to avoid to influence device
performance and reliability.
EVG520HE is a single chamber tool that the maximum size of
procedure wafer is 4 inch, besides it can handle 2 × 2 cm2 chip. It is a
semi-automatic tool that can heat or cool upper and bottom wafer at the
same time. And EVG520HE has individual ramp system to provide
different process temperature to upper and bottom wafer, the maximum
process temperature is 350℃, besides, it can provide compress force up
to 12000Nt for 4 inch wafer to enhance bonding, this tool doesn`t require
vacuum environment to achieve bonding successful.
2-3 Material Analysis Instruments
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I. Scanning Electron Microscopy Hitachi S-4700I
SEM provide an express way to inspect the surface morphology and
the cross section inspect image of the critical layer and the resistive
switching thin films, are characterized by the scanning electron
microscopy (SEM, Hitachi S-4700) with a resolution of 1.5 nm operated
at 15 kV, the outlook of SEM shows at Figure 2-6. We need to coat a thin
Pt layer on the samples before sent them into the chamber of SEM to
enhance conductivity and get a high quality image. The accelerated
electron beam, emitted from a cold-cathode electron gun with the extract
voltage in the range from 0.5 kV to 30 kV, collides with DUT, and the
secondary electrons originated within a few nanometers from the surface
of the DTU are detected and rendered into a bright SEM image, which is
as shown in Figure 2-11.
II. Optical Microscope
Light incident from the object will be enlarged by at least two optical
system such as objective lens and eyepiece, First objective lens to
produce a zoom in real image, and the human eye observe real image that
enlarge by objective lens through the eyepiece. The optical microscope
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can replace the lens, so that the observer can replaced magnification.
These objectives are generally placed on a rotating nosepiece, rotation of
nosepiece can let different lens enter into the optical path reached the
eyepiece. 1600 times became a light microscope magnification, the
maximum limit, making the morphology of the application to be greatly
restricted in many areas. If you want to observe smaller objects, you will
require other methods such as electron microscopy.
III. P-10 Surface Profiler
The P-10 surface profiler is high-resolution equipment that obtain
step height and micron roughness in various applications as shown in
Figure 2-7. It is able to measure micron roughness with 1Å resolution
over short distance over 60millimeter scanning. The P-10 provides the
following features: measurement of vertical features ranging from under
100Å to approximately 0.3 mm with a vertical resolution of 1 or 25Å , a
band pass filter allows the separation of intermediated wavelengths,
minimizing the effects of environmental noise on measurements,
precision mode, allowing precise location of small features,
accommodation of samples up to 355 mm (wide), 63.5mm (thick), and
- 21 -
2.2 kg in weight.
IV. Transmission Electron Microscopy (TEM)
TEM is short for Transmission Electron Microscopy; it is a powerful
tool for materials analysis. The outlook of TEM is shown at Figure 2-8.
From 1930, first TEM is applied into industry, now days the resolution of
TEM can reach 2~3Å with high working voltage about 1000KV. This
nano scale inspection is really important and necessary to semiconductor
development. The working principle of TEM is that electrons have wave
form brought out by Louis de Broglie. The atomic resolution capability
offers an express way to enter nano-scale world. It is commonly used to
materials investigation on morphological observation, crystallographic
study, and elemental identification. The field applications may cover a
wide span from semiconductor, ceramics, metals, alloy, polymer, and
bio-medical materials.
V. Scanning Acoustic Tomography (SAT)
SAT is the short for Scanning Acoustic Tomography and it`s also
called SAM (Scanning Acoustic Microscope) shown at Figure 2-9. The
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working frequency of SAT is MHz level but not the ultrasonic cleaning
that working at KHz frequency. The transmission depth depends on the
raise of frequency to decrease, in normal condition, MHz level ultrasonic
don`t bring cavitation effect so it can`t use at cleaning or agitate fragile
device.
Because this characteristic that MHz ultrasonic don`t cause any
damage to the sample and it can transmit a certain depth of solid or liquid
material to inspect the structure, but ultrasonic is very sensitive to the air
inside the test structure that air can interrupt the transmission of
ultrasonic, so this can applied to check the completeness of chips.
Test structure are soaked in dielectric normally be water, by analyze
the reflex of ultrasonic with software, we can check the line and layer
inside the chip that can`t be seen by bare eye.
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Figure 2-1 Main flow of experimental procedures
(NDL)
Figure 2-2 Outlook of plasma enhanced chemical vapor deposition
- 24 -
(NFC)
Figure 2-3 Outlook of flip chip bonder
(a)
- 25 -
(CNMM)
Figure 2-4 Outlook of (a) EVG 501 (b) the wafer holder of EVG 501
(CNMM)
Figure 2-5 Outlook of EVG 501
(b)
- 26 -
(Hitachi, University of California Riverside)
Figure 2-6 Outlook of scanning electron microscopy
(NDL)
Figure 2-7 Outlook of P-10 surface profiler and information panel
- 27 -
(FEI)
Figure 2-8 Outlook of Transmission Electron Microscope
(HITACHI)
Figure 2-9 Outlook of scanning acoustic tomography (SAT)
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Chapter 3
3D IC Key Technology - Bonding
3-1 Introduction
Bonding process is quite different from the traditional semiconductor
processes. Traditional semiconductor manufacturing process direct make
device on the wafer by multistep deposition, annealing, lithography,
etching to accomplish two dimension device, so all devices are made on
one substrate that limit the function of chip, now days we connect
different function chip by package, but RC delay and interconnect wire is
too long that will lower the performance of electronic system.
Three-dimensional integrated circuits can solve these problems with
bonding and TSV manufacture technique that can integrate different
function chips by just stacking these chips and communicate by through
silicon via (TSV) to reduce communication time efficiently, this is a
potentially method to maintain Moore`s Law. With these reasons mention
above, TSV etching, filling, bonding are the key of 3D-IC integration
efficiently. In this paper, oxide bonding is observed for different species
of oxide pairs, pre-curing solution choice, bonding temperature, given
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force type and magnitude. Among these oxide species, wet oxide is the
prefer candidate that it has a better quality and uniformity, so wet
oxide/oxide species as bonding material is our main point. Eventually,
wet oxide/oxide species bonding and its bonding characteristics will be
spotlighted not only in this chapter but also in the whole content.
3-2 Oxide bonding Mechanism
I. Induction
Silicon oxide layer is an important intermediate for wafer bonding
because of its low contamination and the well-development of film
deposition technique in semiconductor processes. Therefore, oxide
bonding could be an attractive approach of layer transfer in 3D IC.
Compared with polymer bonding, oxide bonding has advantages such as
no ionic contaminant, excellent thermal property, compatible with CMOS
process, and the capability for high density integration. However, the high
process temperature is the major concern for application. It has been
reported that PECVD oxide with lower process temperature could reduce
thermal stress and wafer bow issue [8]. Accordingly, this paper
investigates the relation between bonding quality with PECVD oxide,
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other species and parameters to provide the guidelines for low
temperature oxide wafer bonding.
A successful oxide bonding has many key points to achieve the goal,
such as cleanliness, wafer distortion, oxide film uniformity, etc. The basic
explanation for each reason is as follows
(1) Cleanliness
The bonding process is first deposition a thin film as a bonding layer
on both wafers, then two wafers contact with bonding layer to bonding
layer direction and put force, heat on the wafers to induce diffusion or
deteriorate or chemical reaction to make bonding layer stick to each other.
Metal bonding or eutectic bonding or polymers bonding are all
content contaminant in the view as FEOL, they can display a well
bonding result in BEOL, because these bonding layer are softer compare
with oxide bonding, and they are bonded by diffusion and deteriorate, so
cleanliness isn`t as important as oxide bonding.
(2) Wafer distortion
Oxide can be a good bonding layer material, but the thickness of the
oxide film is very important. Because oxide film has stress, so if the film
is too thick, then wafer will distortion likes a bow, this will reduce contact
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area. For this reason, the bonding area is less correspond to whole flat
wafers, the solution is deposit a proper thickness of oxide film to avoid
wafer bow occur.
(3) Film uniformity
Film uniformity is one of the key point of bonding process, bad film
uniformity will reduce contact area just like wafer bow that the reason
mentioned above already. This situation often occurs at the PECVD tool,
after deposition process the wafer appear Newton ring and this can be
seen by bare eye in most of my experiment, the reason of Newton ring is
that different thickness oxide film shows different color, and in my
experiment, more close to the edge of the wafer appears more rings. We
get a conjecture to why Newton ring often appear at PECVD tool but not
furnace LPCVD, because the product of the chemical reaction falls on the
wafer but not reaction at the wafer surface like furnace LPCVD, so if the
chamber is not big enough or the chamber is not designed for 4 inches
wafer specially, the uniformity problem will exist.
II. Mechanism of oxide bonding process
Oxide bonding is induced at the contact interface with the chemical
- 32 -
reaction formula shown in below:
Si-O-H + Si-O-H Si-O-Si + H2O [9, 10]
When two oxide films contact, the OH groups tend to dissociate to
form H2O molecules and leaves Si-O-Si bonds alone at the interface.
Figure 1 and 2 present the mechanism of oxide bonding. As the small
parts of area bonded, the reaction will propagate into nearby area and
finally the whole wafer if the surface flatness and wafer bow are adequate.
The bonding results could be investigated clearly under the microscope
with IR light source. The edge of bonded area, called bonding wave [11],
will extend from wafer center to edge.
3-3 Experiment Procedure
P-type (100) 4-inch Si wafers were adopted in the study. 3000Å thick
of different oxide species layers (as shown in Table 1) were deposited on
bare silicon wafers after RCA clean (SPM + SC1 + SC2 + HF) for
bonding quality evaluation. These wafers were then sawed into dies. The
dies were dipped in H2O2 solution at 25℃ for different time, and then
bonded under 400℃, 100N for 50min. With the drop test (20cm height, 3
times) pre-assessment, the passed oxide species were further applied for
- 33 -
wafer-level bonding. Table 1 summarizes the assessment results of
different bonding oxide species with various H2O2 dipping time.
Based on the experiment results, PECVD SiH4 oxide is eliminate
from the next experiment and three kinds of oxide species, PECVD
TEOS, LPCVD TEOS and thermal oxide, were chosen to perform
wafer-level bonding. These wafers were first dipped in pre-treatment
solutions H2O2 and modified cleaning solution (SC1 10min + SPM
10min)[9, 12] respectively, and then bonded with different approaches
(EVG 501, EVG 520) with various bonding forces (10kN, 1kN, 40N),
bonding temperature[13, 14], oxide species and pre-treatment solutions.
After bonding, the wafers were investigated with SAT (scanning acoustic
tomography) for bonding quality evaluation. Due to the poor uniformity
at the wafer edge resulted from the Newton ring issue of PECVD facility;
PECVD TEOS to PECVD TEOS bonding could not perform good bond
quality, and LPCVD TEOS can`t provide a good bonding result, too.
Therefore, only the combinations of PECVD TEOS to thermal oxide
bonding and thermal oxide to thermal oxide bonding are adopted and
discussed in the next chapter.
- 34 -
3-4 Result and Discussion
From Table III-I, PECVD SiH4 oxide to PECVD SiH4 oxide bonding
does not perform good bond results with different H2O2 dipping time.
Two possible reasons are suggested. One is PECVD SiH4 causes higher
stress than TEOS oxide, which induces larger wafer bow. The other is the
oxide film property of PECVD SiH4 is more stiff than TEOS oxide,
which makes the inflexibility during bonding and results in poor bonding
integrity.
Figure 3-3 and Figure 3-4 show the SAT image of wet oxide to wet
oxide bonding under 250 ℃, 30 min, 40N with EVG 501 and wet oxide
to PECVD TEOS bonding under 250 ℃, 30 min, 40N with EVG 501,
respectively. These wafers are pre-curing by dipping with H2O2 20 min
and the dark area on SAT image at the wafer means this area are bonded
and the bright area means not bonded. The wafer pairs in this set only
change the parameter of oxide species in bonding process, from SAT
images we can`t see difference obviously, but at the edge of Figure 3-4,
the unbounded area is larger than Figure 3-3, which indicates PECVD
oxide has a worse uniformity.
Figure 3-3 and Figure 3-5 show the SAT image of wet oxide to wet
- 35 -
oxide bonding under 250 ℃, 30 min, 40N with EVG 501 and wet oxide
to wet oxide bonding under 250 ℃, 30 min, 1000N with EVG 520,
respectively. These wafers are pre-curing by dipping with H2O2 20 min
and change the parameter of bonding force and given force type in
bonding process, from SAT images we can`t see difference obviously, too.
To be worth mentioning that EVG 501 is a bonding tool that applies force
(range from 0N to 40N) by a pin and, but EVG 520 is a nanoprint tool
which gives force (range from 0N to 12000N) by a circle pad.
Figure 3-6 and Figure 3-7 show the SAT image of wet oxide to wet
oxide bonding under 250 ℃, 30 min, 40N with EVG 501 and wet oxide
to wet oxide bonding under 250 ℃, 30 min, 1000N with EVG 520,
respectively. These wafers are pre-curing by dipping with SC1 10 min +
SPM 10 min and change the parameter of bonding force and given force
type in bonding process, from SAT images we can`t see difference
obviously, too. The results show that the bonding areas of both two
bonding combinations are large and uniformly distributed, expect few
bubble areas might be caused by particles or contamination. The bonding
failure at the wafer edge is mainly resulted from the non-uniformity of
PECVD TEOS deposition. Compare with Figure 3-3 and Figure 3-6, we
- 36 -
found out that pre-treatment solution is extreme important in oxide
bonding, this conclusion also fits in with the comparison of Figure 3-5
and Figure 3-7. Besides, the results in Figure 3-6 and Figure 3-7 show no
big difference between the two conditions, which indicates both the two
types of bonding tool could be used for oxide bonding, this result can also
be discover in Figure 3-3 and Figure 3-5.
As aforementioned, the more hydroxyl bonds can induce better
bonding strength. Therefore, the modified clean process was adopted
before bonding to enhance the density of hydroxyl bond and remove
particles on the oxide surface. The modified clean process includes two
steps, one is SC1 treatment to remove ionic contaminant, and the other is
SPM treatment to remove the organic contaminant and increase the
density of hydroxyl bond. So modified clean is a better pre-treatment
solution than H2O2.
Figure 3-8 and Figure 3-9 show the SAT image of wet oxide to
LPCVD TEOS bonding under 250 ℃, 30 min, 40N with EVG 501 and
wet oxide to LPCVD TEOS bonding under 400 ℃, 30 min, 40N with
EVG 501, respectively. These wafers are pre-curing by modified clean
and change the parameter of bonding temperature in bonding process,
- 37 -
from SAT images we can`t see difference obviously that bonding quality
is so terrible.
Figure 3-10 and Figure 3-11 show the SAT image of wet oxide to
PECVD TEOS bonding under 250 ℃, 30 min, 40N with EVG 501 and
wet oxide to PECVD TEOS bonding under 400 ℃, 30 min, 40N with
EVG 501, respectively. These wafers are pre-curing by modified clean
and change the parameter of bonding temperature in bonding process,
from SAT images we can see that no significant difference between them
and the bonding quality seems not bad, only a little area is not bonded.
Compare with Figure 3-10 and Figure 3-11 , we found out that bonding
temperature is not a main factor in oxide bonding, this conclusion also
fits in with the comparison of Figure 3-8 and Figure 3-9; besides,
compare with Figure 3-8 and Figure 3-10, it shows that wet oxide to
LPCVD TEOS isn`t a good combination, this result also fits in with the
comparison of Figure 3-9 and Figure 3-11.
Figure 3-12 and Figure 3-13 show the SAT image of wet oxide to
LPCVD TEOS bonding under 250 ℃, 30 min, 1000N with EVG 520 and
wet oxide to LPCVD TEOS bonding under 400 ℃, 30 min, 10KN with
EVG 520, respectively. These wafers are pre-curing by modified clean
- 38 -
and change the parameter of bonding force in bonding process, from SAT
images we can see that higher bonding pressure has a larger bonding area,
and this conclusion also fit in with the comparison between Figure 3-14
and Figure 3-15 which are bonded with condition wet oxide to PECVD
TEOS bonding under 250 ℃, 30 min, 1000N with EVG 520 and wet
oxide to PECVD TEOS bonding under 400 ℃, 30 min, 10KN with EVG
520, respectively.
3-5 Summary
The influence on bonding performance of various bonding
parameters, including oxide species, bonding tool with different given
force model, bonding temperature, and applied bonding force, was
investigated in this study. Both the combinations of thermal oxide to
PECVD TEOS bonding and thermal oxide to thermal oxide bonding can
perform good bonding quality. The bonding performance has no big
difference between the pin type and pad type of bonding tools. In addition,
the larger bonding force can induce larger bonding area with better
bonding performance, but the bonding temperature seems not an effective
factor. The investigation results can provide the guidelines of low
- 39 -
temperature oxide bonding for 3D integration and MEMS applications.
H2O2 dipping time
(min)
Oxide species
20 10 5 1
PECVD TEOS to PECVD TEOS O O O O
Thermal oxide to thermal oxide O O O O
PECVD SiH4 to PECVD SiH4 X X X X
PECVD TEOS to thermal oxide O O O O
Table III-I Oxide bonding combine with different dipping time verse
oxide species match
- 40 -
Figure 3-1 Wafer bow schematic diagram [24]
Figure 3-2 Oxide bonding mechanism schematic diagram
- 41 -
Figure 3-3 SAT image of wet oxide to wet oxide bonding under 40N, 250
℃ and 30min by EVG 501 with H2O2 pre-treatment
Figure 3-4 SAT image of wet oxide to PECVD TEOS bonding under 40N,
250℃ and 30min by EVG 501 with H2O2 pre-treatment
- 42 -
Figure 3-5 SAT image of wet oxide to wet oxide bonding under 40N, 250
℃ and 30min by EVG 520 with H2O2 pre-treatment
Figure 3-6 SAT image of wet oxide to wet oxide bonding under 40N, 250
℃ and 30min by EVG 501 with modified clean pre-treatment
- 43 -
Figure 3-7 SAT image of wet oxide to wet oxide bonding under 40N, 250
℃ and 30min by EVG 501 with modified clean pre-treatment
Figure 3-8 SAT image of wet oxide to LPCVD TEOS bonding under 40N,
250℃ and 30min by EVG 501 with modified clean pre-treatment
- 44 -
Figure 3-9 SAT image of wet oxide to LPCVD TEOS bonding under 40N,
400℃ and 30min by EVG 501 with modified clean pre-treatment
Figure 3-10 SAT image of wet oxide to PECVD TEOS bonding under
40N, 250℃ and 30min by EVG 501 with modified clean pre-treatment
- 45 -
Figure 3-11 SAT image of wet oxide to PECVD TEOS bonding under
40N, 400℃ and 30min by EVG 501 with modified clean pre-treatment
Figure 3-12 SAT image of wet oxide to LPCVD TEOS bonding under
1000N, 250℃ and 30min by EVG 520 with modified clean pre-treatment
- 46 -
Figure 3-13 SAT image of wet oxide to LPCVD TEOS bonding under
10KN, 250℃ and 30min by EVG 520 with modified clean pre-treatment
Figure 3-14 SAT image of wet oxide to PECVD TEOS bonding under
1000N, 250℃ and 30min by EVG 520 with modified clean pre-treatment
- 47 -
Figure 3-15 SAT image of wet oxide to PECVD TEOS bonding under
10KN, 250℃ and 30min by EVG 520 with modified clean pre-treatment
- 48 -
Chapter 4
Ultra-Thin Silicon Layer Transfer
Procedure
4-1 Introduction
When the devices are scaling down to fill the bill of Moore`s law and
reach the goal of higher speed, lower power, higher density, etc. But in
the path of chasing this goal, the problem of scaling down appears, such
as drain-induce-barrier-lowering (DIBL), nonzero sub threshold slope,
on/off current speed too low, leakage, etc. But if use transferred silicon
layer on buried oxide as the substrate, these problems can get alleviation,
furthermore, it can increases the transistor switching speed of a transistor
by burying a oxide layer below the source, base, and drain of the
transistor to isolate it from the substrate, increase electron mobility,
reduce power consumption, etc. These benefits mentioned above can
provide a flexible design space to tradeoff between the power saving and
device performance.
4-2 Mechanism of silicon split
- 49 -
We implant 1H ions into silicon substrate with a proper energy, the
implant energy is expected to let these ions stop at the depth which we
want to. These ions are trap in silicon substrate in 1H state, when this
wafers are sent into anneal, these ions will diffuse, once 1H ions contact
to each other, they will form H2 molecule and won`t dissociate into 1H
again, because it needs 435KJ/mol to return two 1H atoms, so H2
molecules won`t become two 1H ions and diffuse through dangling bond
inside the silicon substrate. Implanted ions will present a Boltzmann
distribution, but in the anneal process, ions in the middle of distribution
will form H2 molecules more faster than the edge of the distribution tail,
once H2 exists, 1H ions concentration nearby will become lower, so outer
H ions will diffuse toward to the position that we expect implant depth,
then more H2 molecule form, after a space will form lots of small cavities
at the implant depth layer. As soon as the amounts of H2 cavities reach a
certain quantity, the silicon will split by stress and leaves two parts [15,
16, 17] like Figure 4-1 shows. The concern of implant dose is that if it`s
too low, then the silicon won`t split or anneal temperature must higher,
this condition lead to it will not split; if it`s higher than 2.0 × 1017
ions/cm2[18, 19], after anneal process, blister will appear on the wafer
- 50 -
surface like Figure 4-2 shows, then the process can`t continue cause
unflatten surface[20].
4-3 Experimental Procedure
Standard clean for wafers are performed before implant 1H to wafer
A with two recipes, implant energy 370KeV/expect depth 4μm/dosage
9E16/implant species 1H+ and implant energy 120KeV/expect depth
1μm/dosage 6E16/implant species 1H+[19], The depth corresponding
energy is determined by TRIM[15]. Trim is software written by James F.
Ziegler which is a powerful tool for implantation process. After
implantation, implanted wafers are sent to do SIMS (Secondary Ion Mass
Spectrometry) to identify doping profile, and then deposit 3000Å TEOS
on the silicon substrate A and 3000Å wet oxide on the other silicon
substrate B. Then dicing wafer A and B into chips A and B, chips A are
larger than chips B, the reason why we care about chips sizes is that these
chips need to dip in HF so we coat with adhesive on it to prevent is from
debond in the coming procedure. And then dip these two chips A and B in
SC1 10 min then SPM 10 min, after dip pre-curing solutions is bonding
process, wafer A and B are bonded with oxide to oxide. Oxide layers
- 51 -
from wafer A and B are bonded together and form one complete oxide
layer as buried oxide layer, and then this bonded wafer pair is dipped in
HF for 12 hour to etch silicon defect[23], this addition curing can lower
the following up anneal temperature. This chip pair is sent to furnace to
do anneal procedure at 400℃ for 9 hours and do SIMS analysis again
after annealing to check profile. As the mechanism that mentioned above,
H2 cavities form at the highest doping concentration position, once the
number of the cavities surpasses tipping point, wafer A will split into two
parts, because we do implant and deposit from the front side of wafer A,
so the front side of wafer A will split from the highest H2 concentration
and stick to wafer B, the rest part of wafer A can do next silicon film
transfer process as implant side. These chips are polished and then sent to
FIB (Focus Ion Beam) to prepare TEM samples, use TEM we can see the
whole structure precisely and check if there are defects exist in the
transferred silicon film or not.
4-4 Results and Discussion
I. SIMS analysis
SIMS can measure vertical doping profile after implantation to check
- 52 -
doping concentration, depth and dosage is fitting in with our expectation
or not. We do SIMS analysis after implantation with recipes, each recipe
is implant energy 370KeV/expect depth 4μm/dosage 9E16/implant
species 1H+, implant energy 120KeV/expect depth 1μm/dosage
6E16/implant species 1H+ and the SIMS data are show at Figure 4-3 and
Figure 4-4, respectively. The results are very close to expectation which is
confirmed by SIMS data. And we do SIMS again after anneal procedure
to check the concentration of H atoms which shows in Figure 4-6 and 4-7
for 4μm implantation and the direction of SIMS data are define by Figure
4-5. The result shows that the highest H atom concentration doesn`t
changes its position in depth verse peak of doping concentration diagram
after anneal procedure. We can observe obviously that silicon split at the
highest doping concentration position.
II. SEM
After oxide film deposited, bonding procedure, anneal, these chips
are sent to SEM to check oxide thickness and whole structure, but it can`t
be seen obviously in SEM. Just take some picture that can barely
recognize the thickness of oxide layer, these picture shows at Figure 4-8.
- 53 -
Figure 4-9 shows that transferred silicon surface spread hill like shape
roughness and we give it a conjecture that it relates to defect shape which
is seen by TEM.
III. TEM
In TEM, we can see every layer about their thickness, oxide bonding
interface, transferred silicon defect. We had sent chips that implanted
1μm after bonding procedure and after silicon split to check the
difference. Figure 4-10 shows the whole structure of the chip before split
and the thickness of each layer is shown in Figure 4-11, the white area in
oxide film is not oxide interface but the scar in sample preparation for
TEM, so we will focus on the left side of the sample which is shown in
Figure 4-10. There is nearly no oxide interface can be seen in TEM show
at Figure 4-12 which indicate that oxide bonding quality with this
procuring method is pretty good. Figure 4-13 (a) and (b) show the defects
contain area, these defect are mainly line defects which form triangle
appearance, which thought to be relative with Figure 4-9. Figure 4-14
shows that these defects length range is about 10 ~ 20 nm, and we had
checked if defects exist at the bottom of transferred silicon film, the
- 54 -
position and result are shown at Figure 15 (a) and (b), respectively, which
prove that there is no defect existence. The other chip is already
transferred, Figure 4-16 is the whole structure diagram and the thickness
of each layer are shown at Figure 4-17, oxide bonding interface was
confirmed at Figure 4-18 which indicate perfect oxide bonding result.
Transferred silicon film doesn`t exist defect no meter at top of the film
proved by Figure 4-19 (a) and (b), but in the chip after bonding can
observe defects at the end of implant path. Defects don`t exist at the
transferred silicon film, the reason is that it already dipped in HF for
defect etch and this chip is annealed, so it contains no defect. But defect
exist at the chips just after bonding procedure, there are two mechanism
about defect produce, because when the implant ions are just enter silicon,
these ions are slow down by electron stopping power (ion energy > 10eV),
when electron stopping power domain, ions collide with electrons of the
lattice atoms, incident ion path is almost unchanged, energy transfer is
very small and crystal structure damage can negligible. But when nuclear
stopping power domain (ion energy < 10eV), then ions collide with
atomic nucleus of the lattice atoms, scattering occurs significantly and ion
path will change randomly so ions causes crystal structure damage near
- 55 -
the depth of 1μm. From the mechanism described above, we expect
defects exist at the end of implant path, and in TEM images we can see
defects at the specific position that we expect.
- 56 -
Figure 4-1 Ideal split off scheme
Figure 4-2 Blistering occur scheme
- 57 -
Figure 4-3 Implant depth 370KeV(4μm)/9E16/1H+
Figure 4-4 Implant depth 120KeV(1μm)/6E16/1H+
- 58 -
Figure 4-5 SIMS data direction definition
Figure 4-6 After silicon split after 400 ℃ anneal
- 59 -
Figure 4-7 After silicon split after 400 ℃ anneal
Transferred Si layer
PECVD TEOS
Wet oxide
(a)
- 60 -
Figure 4-8 (a) (b) Oxide thickness confirm by SEM
Figure 4-9 After silicon split surface
(b)
PECVD TEOS
Wet oxide
Transferred Si layer
- 61 -
Figure 4-10 Before silicon split cross section overview
Figure 4-11 Before silicon split layer thickness confirm
- 62 -
Figure 4-12 Before silicon split oxide bonding interface
(a)
- 63 -
Figure 4-13 Before silicon split (a) silicon defect position (b) silicon
defect
(b)
(a)
- 64 -
Figure 4-14 (a) (b)Silicon defects before annealing process
(a)
(b)
- 65 -
Figure 4-15 Before silicon split (a) defect check position (b) interface
between silicon and oxide
Figure 4-16 After silicon split overview
(b)
- 66 -
Figure 4-17 After silicon split thickness check
Figure 4-18 After silicon split oxide bonding interface
- 67 -
Figure 4-19 After silicon split (a) defect check position (b) defect check
(a)
(b)
- 68 -
Chapter 5
Conclusions and Future Work
5-1 Conclusions
Three-dimensional integrated circuit is a new technology that
provides significant performance and improves functional benefits such
as high device integration density, interconnectivity, heterogeneous
integration technologies, and a reduction in length of the long global
wires. In this thesis, oxide bonding parameter, like bonding temperature,
given force magnitudes, given force types, procuring solution are all
demonstrated. Dip in SC1 10 min + SPM 10 min procuring solution can
improve bonding area obviously, choose PECVD TEOS + wet oxide
match can have a good bonding result and the more given bonding force
will reach a larger bonding area.
Then choose 5.0 × 1016
ions/cm2 dosage with 120KeV implant
energy combine HF dip 9 hours and anneal at 400℃, we can get a perfect
ultra-thin silicon layer transfer that silicon film is only 1μm and this film
is single crystal with surface only exist small roughness and oxide
bonding quality is so good that oxide bonding interface can`t be examine
- 69 -
on TEM, this ultra-thin silicon film transfer process can continue to
accomplish a good performance device.
5-2 Future work
Continue process to achieve wafer-level ultra-thin silicon film
transfer and keep put the effort on lower bonding and anneal temperature
to 250℃ or reach a thinner silicon film on oxide layer, then analysis
about thin film stress, mechanical structure strength and lattice inspect.
After thin film silicon transfer procedure is mature, design a compatible
process to integrate BSI-CIS on it. If this terminal purpose can be reached,
then this easy and convenient bonding technology will have a lot of
applications for 3D-IC.
- 70 -
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簡歷(Vita)
姓名: 何星漢 (Hsing-Han Ho)
性別: 男
出生年月日: 民國 77 年 04 月 09 日
籍貫: 台中市
學歷: 國立中山大學物理系 (2006.9-2010.6)
國立交通大學電子工程研究所 (2010.9-2012.8)
碩士論文題目:
超薄化矽轉移與氧化矽接合在背照式感光元件
上之應用
Ultra-Thin Silicon Layer Transfer with Oxide Bonding
for BSI-CIS Application