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ORIGINAL PAPER
Tribological Behavior of Carbide-derived Carbon Coating on SiCPolycrystal against SAE52100 Steel in Moderately Humid Air
Fei Gao Æ Jinjun Lu Æ Weimin Liu
Received: 6 March 2007 / Accepted: 4 June 2007 / Published online: 23 June 2007
� Springer Science+Business Media, LLC 2007
Abstract In this article, carbide-derived carbon coating
(CDC) on a substrate of silicon carbide was produced by
chlorination at 1000 �C. The influence of dechlorination on
the friction and wear of CDC coating sliding against
SAE52100 steel was investigated. It was found that
dechlorination is crucial and necessary for obtaining good
tribological performance of CDC coating against steel. The
CDC coatings exhibit excellent tribological performance in
air at loads lower than 30 N and provide good protection
from wear damage of steel as well. The tribological per-
formance of CDC coating against steel is superior to that of
commercially available graphite.
Keywords Carbide derived carbon � Friction and wear �Steel
Introduction
Tribology of carbon is always an attractive and challenging
field to tribologists. Tribology of carbon (graphite, dia-
mond, diamond-like carbon, and fullerene) nowadays
covers a wide range of topics: from additive for oil and
grease, solid lubricant for composites, and, in the past
decades to low- and super-low-friction carbon coatings
[1–5]. Recently, carbide-derived carbon (CDC) has
received attention due to its excellent tribological perfor-
mance [6–12]. According to the definition, CDC is a pure
carbon material produced by selective extraction of metal
atoms from a carbide crystal lattice by halogens, super-
critical water, oxygen at a low-partial pressure, other et-
chants, or in vacuum [6]. The advantages of CDC coating
over carbon coating by conventional vapor deposition
techniques are in many aspects: high growth rate, good
coating adherence, unlimited thickness, no delamination of
coatings, and no risk of high residual stress [7]. Meanwhile,
CDC coating by high-temperature chlorination of SiC
without hydrogen is believed to have an excellent tribo-
logical performance in both humid and dry air [7]. CDC
coating on top of carbides is found to be versatile as a solid
lubricant in various environments, from dry air to high
humid air [7, 12] and is expected to find many related
applications. It should be pointed out that the counterbody
used in previous studies was silicon nitride [7–12], which is
hard, chemically inert, and easily surface finished. Up to
now, no attempt has been made to investigate the friction
and wear of CDC coating sliding against steel which is
widely used and is subject to chemical attack. Since CDC
has a nanoporous structure and a surface of high-specific
surface area [6], it allows adsorption of different kinds of
gases, such as chlorine. However, there is no information
on what kind of influence the adsorbed gases could have,
especially when the counterbody is made of steel. There-
fore, a systematic investigation of the friction and wear
behavior (wear of the coating is included in this paper) of
CDC coating sliding against steel is necessary. In this
article, a CDC coating on a-SiC was prepared by chlori-
nation at 1000 �C in a flowing gas Ar-5%Cl2. The influence
of dechlorination of the coating on the friction and wear in
moderately humid air is undoubtedly a very important part
of this work. Commercially available graphite was used as
F. Gao � J. Lu (&) � W. Liu
State Key Laboratory of Solid Lubrication, Lanzhou Institute of
Chemical Physics, Chinese Academy of Sciences, Lanzhou
730000, P.R. China
e-mail: [email protected]
F. Gao
Graduate School of the Chinese Academy of Sciences, Beijing
100039, P.R. China
123
Tribol Lett (2007) 27:339–345
DOI 10.1007/s11249-007-9240-y
the baseline for comparison of the tribological test results.
The friction and wear of the CDC coating against steel in
moderately humid air are investigated and discussed.
Experimental Details
Materials
The a-SiC block (98 wt.% purity) is commercially avail-
able from Shanghai Institute of Ceramics, Chinese Acad-
emy of Sciences. It is fabricated via pressureless sintering.
The density is 3.12 g/cm3. Before chlorination, the SiC
samples were sectioned into 20 · 10 · 2 mm cubes, fol-
lowed by grinding (diamond wheel) and polishing (dia-
mond paste) to a surface roughness Ra of 0.02 lm.
Silicon nitride balls and SAE52100 balls (HRC60-65)
used in this study are commercially available from
Shanghai Institute of Materials, China. All the balls have a
diameter of 3 mm. The surface roughness (Ra) of Si3N4
ball and SAE52100 ball are 0.02 and 0.08 lm, respec-
tively. As the baseline for tribological tests, commercial
graphite available from Shanghai Sxcarbon Technology
Co., Ltd was chosen. This material is considered as a 3H-
carbon material and can be used in many friction-reducing
applications. The 3H means high purity in graphite, highly
dense, and high strength. The density is 1.80 g/cm3 and
compressive strength is 72.6 MPa.
Preparation of CDC Coating
The apparatus used for preparation of CDC coating is de-
signed and manufactured according to previous literature
[6]. In order to perform the chlorination, the sectioned SiC
samples were exposed to flowing gas Ar + (4–5)% Cl2 for
20 h. Every step is strictly controlled to make sure the
reaction is correctly performed. For example, it is neces-
sary to pre-purge Ar gas through the reaction tube for at
least 30 min before the experiment. In this study, a heating
rate of 50 �C per min was used. Dechlorination was per-
formed to remove residual Cl2 in the coating [6]. In order
to study the effect of the adsorbed Cl2 on the friction and
wear of the CDC coating, some samples without dechlo-
rination were deliberately used for tribological tests. X-ray
photoelectron spectroscopy (XPS, PHI-5702, Physical
Electronic, USA) is used to evaluate the surface before and
after dechlorination since it is a surface sensitive tool. A
thin gold coating (less than 2 nm in thickness) is sputtered
on the CDC coating before XPS. The peak of Au4f is used
as the internal standard for calibration. Meanwhile, it is
necessary to ultrasonically clean the CDC coating in an
acetone bath to remove the loosely attached, powdery top
carbon layer, as described in the literature [7]. The average
surface roughness of the CDC coating is 2.26 lm, which
indicates a very rough surface after the chlorination. For
tribological tests, very careful polishing on paper (manual
polishing, A4 paper) was used to make the average surface
roughness of the CDC coating to be 0.85 lm. The pol-
ishing was done dry and without polishing compound.
Meanwhile, due to the ability to self-adjust to the count-
erbody of the CDC coating produced in pure chlorine [7],
CDC coatings with high-surface roughness were used.
Friction and Wear Tests
Friction and wear tests were performed on a UMT-2MT
tribo-meter (CETR, USA) with a ball-on-disk configuration
at 20–21 �C in air (relative humidity is 49–51%). The ball
which is made of either SAE52100 or Si3N4 with a diam-
eter of 3 mm, makes oscillating movement (5 mm in
amplitude) on the top of CDC coating or commercially
available graphite. The tribological tests were conducted
with varied normal loads (2–40 N) and frequencies
(2–20 Hz, corresponding from 0.02 to 0.2 m/s in sliding
speed). All the specimens were ultrasonically cleaned in an
acetone bath prior to the tribological tests. A MicroX-
AM 3D profiler was used to measure the worn volumes of
the disks after friction and wear testing. The diameters of
the wear scars on the test balls were measured on an optical
microscope and were converted to wear volumes. All wear
rates were calculated based on the worn volumes and the
sliding distance. The worn surfaces were investigated by
using scanning electron microscopy (SEM, JSM-5600LV
JEOL).
Results and Discussion
Effect of Dechlorination on the Tribological
Performance
Figure 1 shows the XPS spectra of the CDC coating before
and after dechlorination. It is clear that the adsorbed Cl2 in
the coating could be totally removed by means of dechlo-
rination. Another result of the dechlorination might be the
partial removal of the adsorbed oxygen species, which is
based on the fact that there was pronounced reduction of
O1s peak and O auger line after dechlorination. As a matter
of fact, the outermost surface of the CDC coating was loose
in structure and had a high-surface area, which enabled
adsorption of different gases. The adsorbed species, such as
O2, H2O, etc., may have some influence on the tribological
behavior of the CDC coating. However, more experiments
and very detailed discussion are necessary to make it clear.
340 Tribol Lett (2007) 27:339–345
123
Figure 2 shows the typical friction coefficient as a
function of sliding time of CDC coating against SAE52100
steel before and after dechlorination. It is not surprising to
see that dechlorination is very crucial for improved fric-
tional behavior of CDC coating sliding against steel. The
friction coefficient was higher than 0.25 and unstable
(fluctuated after 4,000 s) for samples with no dechlorina-
tion. After dechlorination, the friction coefficient was as
low as 0.15 and remains very stable even after 5 h. The
chemical attack of Cl2 on the steel caused severe corrosion,
and therefore, severe wear (the diameter of wear scar of
steel ball was 1.31 mm) as steel slides against CDC coating
without dechlorination.
Unlike 52100 steel, Si3N4 showed similar tribological
behavior sliding against CDC coatings with and without
dechlorination. The friction coefficients of the CDC coat-
ings without dechlorination treatment sliding against Si3N4
balls at 5 N, 10 N, and 30 N (at a fixed speed of 0.02 m/s)
were 0.14, 0.13 and 0.11, respectively. For the CDC
coatings sliding against Si3N4 balls under the same con-
ditions, friction coefficients were 0.13, 0.11, and 0.10,
respectively. In all cases, the wear of Si3N4 balls was too
low to measure. It is clear that dechlorination of CDC
coatings was not necessary for the CDC/Si3N4 tribo-cou-
ples. It is, due to the chemical inertness and resistance to
corrosion of Si3N4 balls. This result is in good agreement
with previous results [8].
Friction and Wear after Dechlorination
Effect of Load
Figure 3a shows friction coefficients of the commercially
available graphite and CDC against SAE52100 under dif-
ferent loads. The friction coefficients of the commercially
available graphite against SAE52100 were in the range
from 0.23 to 0.27 and seemed to be independent of normal
load. The friction coefficients of the CDC coating sliding
against SAE52100 were in the range from 0.12 to 0.14
under the given loads. It is clear that the typical friction
coefficients of SAE52100 against the CDC coating were
only half of the values of the same steel against commer-
cially available graphite.
Figure 3b shows the wear rates of the commercially
available graphite and the CDC coating against SAE52100
under different loads. The commercially available graphite
showed poor wear resistance under the given loads. In
addition, the wear rates of the commercially available
graphite increased very rapidly with increasing normal
loads. For example, the wear rate of the commercial
graphite at 5 N is on the order of 10–4 mm3m–1 while the
wear rate at 10 N was on the order of 10–3 mm3m–1. In
contrast, the CDC coating exhibited very good wear
resistance, especially at 5 N and 10 N. Although the wear
rates of the CDC coating increased considerably at loads of
30 N and 40 N, the values were still very low compared to
that of the commercially available graphite.
Figure 3c shows the wear rate of SAE52100 sliding
against commercially available graphite and the CDC
coating. It is important to measure the wear rate of the steel
in order to make a comparison on the lubricity of the
commercially available graphite and the CDC coating. As
seen in Fig. 3c, the CDC coating provided good protection
from wear damage of the steel ball, even at 30 N and 40 N.
In this sense, the tribological performance of the CDC
coating was superior to that of the commercially available
graphite.
Fig. 1 XPS spectra of the surface of the CDC coating before and
after dechlorination
Fig. 2 Typical friction coefficient as a function of sliding time of the
CDC coating sliding against SAE52100 steel before and after
dechlorination
Tribol Lett (2007) 27:339–345 341
123
Effect of Speed
Figure 4 shows the influence of sliding speed on the fric-
tion and wear of the commercially available graphite and
the CDC coating sliding against SAE52100. In both cases,
the friction coefficients tend to decrease as speed increases
from 0.02 to 0.2 m/s (Fig. 4a). For the commercially
available graphite, friction coefficients at 0.02 m/s and
0.20 m/s are 0.24 and 0.13, respectively. For CDC coating,
the friction coefficients at speeds higher and equal to
0.10 m/s were lower than 0.10, which makes the CDC
coating very attractive for many applications.
As seen in Fig. 4b, the wear rates of the commercially
available graphite tended to decrease as the speed
Fig. 3 Tribological properties of the commercially available graphite and the CDC against steel under different loads at 0.02 m/s (a) friction
coefficient, (b) wear rates of the commercial graphite and the CDC coating, (c) wear rate of steel
Fig. 4 The influence of speed on the friction and wear of the commercially available graphite and the CDC coating sliding against steel a)
friction coefficient, b) wear rate
342 Tribol Lett (2007) 27:339–345
123
increases, e.g. from 1.90 · 10–3 mm3m–1 at 0.02 m/s to
2.43 · 10–4 mm3m-1 at 0.20 m/s. The wear rates of the
CDC coating were substantially lower compared with those
of the commercially available graphite. The wear rates of
the CDC tended to decrease as the speed increases; how-
ever, the wear rate of the CDC at 0.20 m/s was consider-
ably higher than at other lower speeds, as shown in Fig. 4b.
It would be reasonable to make a tribological test at speeds
higher than 0.20 m/s to see what happens. However, 20 Hz
(0.20 m/s) was the highest frequency that could be em-
ployed for the tribometer.
For a tribological test with oscillating movement, higher
speed means a shorter time for exposure to ambient gases.
In other words, the time for the readsorption of gases on
worn surface is inversely proportional to the sliding speed.
The fact of low-friction coefficient at high speed might be
related to the adsorption and desorption of gases. The
higher-contact temperatures that occur at higher-sliding
speeds may have an influence on friction. Those higher
surface temperatures could affect the tribochemical
behavior (adsorption and desorption of gases as well as
oxidation) and the mechanical behavior of the contacting
materials.
Worn Surface
Figures 5a and 5b show the worn surfaces of the com-
mercially available graphite and the CDC coating at 30 N
and 0.02 m/s. The worn surface of the commercially
available graphite in Fig. 5a was typical and was charac-
terized by many crevices. Plastic deformation could also be
found in Fig. 5a. However, it should be noted that the
crevices, which were the consequence of the cracks initi-
ated from the sub-surface and plastic flow, gave birth to a
large number of wear particles, and thereby, yielded high-
wear rate. For the CDC coating, the worn surface at 30 N
and 0.02 m/s was free of cracks and was characterized by
plastic deformation, see Fig. 5b. It was smooth with only
several plastically deformed grooves along the sliding
direction (the grooves correspond to the abrasion of hard
particles or asperities on the surface of SAE52100 ball, see
Fig. 5b). The worn surfaces of the CDC coating at low
loads (e.g. 5 N and 10 N) were very smooth in the contact
areas (Fig. 5c).
Figure 6 shows the worn surfaces of steel balls after
sliding against CDC coating with and without dechlorina-
tion, as well as commercial graphite. The diameter of the
wear scar on steel ball against CDC coating before,
dechlorination was much bigger than that on steel ball
against CDC coating after dechlorination, Figs. 6a and 6b.
Meanwhile, it can be seen that the worn surface of steel
ball, in Fig. 6a was covered by, tribochemical products
(Fig. 6a). At 5 N and 0.02 m/s, the worn surface of steel
ball was smooth (Fig. 6b). However, several grooves par-
allel to the sliding direction can be found on the worn
surface of steel ball under high load (30 N in Fig. 6c). As
seen in Figs. 6b, 6c and 6d, wear particles on steel ball in
sliding against commercial graphite were much more than
on steel ball against CDC coating.
Fig. 5 SEM micrographs of the worn surfaces of a) the commercially
available graphite at 30 N and 0.02 m/s, b) the CDC coating at 30 N
and 0.02 m/s, and c) the CDC coating at 40 N, 30 N and 10 N (wear
tracks from left to right)
Tribol Lett (2007) 27:339–345 343
123
Comparison
In this work, the tribological behavior of the CDC coating
sliding against SAE52100 in air at moderately relative
humidity has been investigated. Commercially available
graphite which is used as the baseline for the tribological
tests, exhibited considerable friction-reducing ability at low
loads and high speeds. However, the wear resistance of the
graphite could hardly meet the requirements of many tri-
bological applications. The cracks initiated from the sub-
surface and their propagation were responsible for the high
wear of the commercially available graphite. The CDC
coating, however, which is composed of nested fullerenic
structures [8], described as carbon onions [9–10], had low
friction coefficient. Plastic deformation, rather than crack
initiation and propagation, were extremely useful for
maintaining low wear of the coating (Figs. 5b and 5c). The
fact that the wear rates of CDC coating increased rapidly at
loads higher than 30 N might be attributed to the structure
of the coating. For a CDC coating with a thickness of
90 lm (after removal of the loosely attached top layer), a
black carbon layer, which was not as dense as the gray
carbon layer underneath, is less than 10 lm in thickness.
The cross-sectional image of CDC coating shows black
carbon layer and gray carbon layer by using a field emis-
sion scanning electron microscopy (FESEM), as shown in
Fig. 7. The load-bearing capacity of CDC coating might be
determined by the black carbon layer but is not the topic of
this article.
Conclusions
Carbide derived carbon coatings with 90 lm thickness
were synthesized on SiC by chlorination at 1000 �C.
Dechlorination was found to be crucial and necessary for
Fig. 6 SEM micrographs of the worn surfaces of SAE52100 sliding against a) the CDC coating before dechlorination at 5 N and 0.02 m/s, b)
the CDC coating after dechlorination at 5 N and 0.02 m/s, c) the CDC coating after dechlorination at 40 N and 0.02 m/s, and d) the
commercially available graphite at 10 N and 0.10 m/s
Fig. 7 FESEM micrographs of the cross-sectional view of the CDC
coating
344 Tribol Lett (2007) 27:339–345
123
the tribological performance of CDC coating in sliding
against steel. CDC coatings exhibited excellent tribologi-
cal performance in air at loads lower than 30 N and
provided good protection from wear damage of steel as
well. The tribological performance of CDC coating
against steel is superior to that of commercially available
graphite.
Acknowledgment The present work is financially supported by,
National Natural Science Foundation of China (No. 50675216) and
Xibuzhiguang of Chinese Academy of Sciences 2003.
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