Discrete modified nanostructural wearproof coatings Ti-N-Cu with crystallites size from 100 to 20 nanometers formed with ion-plasma vacuum-arc method. Copper amount in the received coatings made from 0 to 20 at. %, their hardness have considerably increased up to about 40-45 hPa in comparison with 20-22 hPa for Ti-N coverings. In this work, processes of structure and phase formation of Ti-N-Cu system coatings in a wide interval of copper concentration are investigated.
When you are citing the document, use the following link http://essuir.sumdu.edu.ua/handle/123456789/3531

Belov, D.S.

Blinkov, I.V.

Michalski, J.

Volkhonskiy, A.O.

Electronic Sumy State University Institutional Repository

PROCEEDINGS OF THE INTERNATIONAL CONFERENCE  NANOMATERIALS: APPLICATIONS AND PROPERTIES Vol. 2 No 2, 02FNC07 (4pp) (2013)  2304-1862/2013/2(2) 02FNC07 (4) 02FNC07-1  2013 Sumy State University Discrete Modified Nanostructural Wearproof Coatings TiN-Cu  D.S. Belov1,*, I.V. Blinkov1,†, A.O. Volkhonskiy1,‡, J. Michalski2  1 National University of Science and Technology “MISiS”, Department of functional and high-temperature materi-als, 4, Leninskiy Ave., 119049 Moscow, Russian Federation 2 Institute of Precision Mechanic, 3, Duchnicka St., 01-796 Warsaw, Poland  (Received 20 May 2013; revised manuscript received 05 June 2013; published online 31 August 2013)  Discrete modified nanostructural wearproof coatings Ti-N-Cu with crystallites size from 100 to 20 na-nometers formed with ion-plasma vacuum-arc method. Copper amount in the received coatings made from 0 to 20 at. %, their hardness have considerably increased up to about 40-45 hPa in comparison with 20-22 hPa for Ti-N coverings. In this work, processes of structure and phase formation of Ti-N-Cu system coatings in a wide interval of copper concentration are investigated.  Keywords: Wearproof coating, Titanium nitride, Copper, Nanostructuring, Hardness, PVD method, Nanoindentation.   PACS numbers: 68.37. – d, 68.37.Hk, 68.55.Nq.                                                            * LightningN4S@yandex.ru † biv@misis.ru ‡ abwest@yandex.ru 1. INTRODUCTION  Nanostructuring of nitride coatings (their prepara-tion with a size of grains less than 100 nanometers) of various functional purpose makes it possible to imple-ment in them high values of hardness combining with plasticity. This thereby provides the added performance of wear resistance in conditions of both constant, and fatigue loads [1, 2, 3]. One of the possible ways to limit growth of coating material grains during its deposition is implementation to the forming coating the components which will be spread over the surface of main coating phase nucleus and limit their growth [4, 5, 6]. The main criteria for choosing these modifying agents are lack of noticeable dissolution in a nitride phase and tendency to nitride formation. This work includes researches on studying of struc-ture and properties of TiN-Cu coatings with copper wide concentration range received by a method of ion-plasma vacuum-arc deposition on the hard-alloy cut-ting tool TT10K8B, including its tests for firmness conducted when cutting.  2. RESEARCH TECHNIQUE  Coatings were overlied on an ion-plasma vacuum-arc unit of Bulat type, including three evaporative cathodes with separators of a drop phase in the atmos-phere of reaction gas nitrogen (PN2  3 10-3 Pa). Cath-odes from VT-5 alloy, copper and combined from VT-5 alloy with insertion from Cu were used. The current of evaporative arc (Id) was 120 A, the negative bias (Uc) energized to the substrate, changed from -80 V to – 140 V. Time of coating sputtering was about 90 minutes, their thickness was within 3.9−4.1 micrometers. Morphology, structure of coatings was studied using a field raster electron microscope JSM-6700F with an add-on for energy-dispersive spectrometry JED-2300F, JEOL.  To determine phase composition of a coating the imaging with DRON-4 diffractometer was carried out using СоКα emission and the graphite monochromator on the diffracted beam in asymmetric geometry (the angle between the incident ray and sample surface being   5º).  To carry out structural surveys of coatings the transmission electron microscope JEM 2100 of high resolution, JEOL, Japan was applied.  For sample thinning ion etching was used.  Ion etching was carried out by means of the PIPS equip-ment (Precision Ion Polishing System, Gatan).  Coatings hardness (H) and elastic modulus (E) were measured by the method of continuous indentation at light loads. This test was performed using microiden-tometer Micro-Hardness Tester (CSM Instruments) with fixed loading 300 mN. Indetor penetration depth was controlled so that it did not exceed 10  of coating thickness to restrict substrate material influence.  3. RESULTS AND THEIR DISCUSSION  Appearance of the created coatings does not differ from appearance of the ion-plasma coatings which does not contain metal phase [7]. They have a cell structure with roughness (Ra) of about 0.3-0.2 microns (Fig. 1). Coatings containing 20 at.  of copper have rather porous structure which density increases with reduc-tion in copper amount. Copper amount at fixed Id values  120 A and Uc  – 120 V varied in a coating from 0.6 to 20 at.  when using the respective cathodes, due to area ratio change of evaporating cathodes coatings - VT-5 and copper alloy from 5 to 1. Uc growth from-80 to-140 V, (bringing to energy increase of the sprayed ions bom-barding the substrate) when preserving the identical area ratio of cathode surfaces from VT-5 and Cu (2.4), and also current of evaporating them electric arches  D.S. BELOV, I.V.BLINKOV, А.О. VOLKHONSKY, J. MIKHALSKY PROC. NAP 2, 02FNC07 (2013)   02FNC07-2 (120A) led to reduction of copper amount in a coating from 9 to 1.7 at.  in case of its regular distribution on all substrate surface. Thus nitrogen amount in a coat-ing in relation to a nitride composing element – titan - also decreased (from 0.91 to 0.86). The increase in non-stoichiometry TiN is also supported by the lattice con-stant equal to 4.239 and 4.207 Ǻ respectively for the coatings received at Us-80 and – 140 B. This effect is connected with preferable spraying from a coating both the easiest element - nitrogen, and the copper, which bond energy is less than bond energy of titan in nitride.    Fig. 1 – External appearance of Ti-Cu-N coatings with copper: а) 20 at. %; b) 9 at. %; c) 3 at. %  The x-ray phase analysis speaks for availability in all the samples the titanium nitride and copper if its amount in the coating is from 20 to 9 at. . In case of smaller copper amounts, the lines of its x-ray diffrac-tion are absent on roentgenograms. The level of nitride phase microdeformations of a coating because of copper amount (Figure 2) varied from 0.5 to 1.08 .    Fig. 2 – Change of microdeformations TiN level in TiN–Cu coating depending on copper amount  Reduction of their values with increase of copper amount in a coating can be connected with relaxed influence on them by plastic metal phase. Sizes of the stretching macrostresses in the received coatings, de-termined by the sin2  method, made from 60  40 to 90  40 MPa that speaks for absence of stress in them. The sizes of composite nitride phase development are of about 15 nanometers and very little depend on coating copper amount. In Figure 3, you see the images received by TEM method, crystallites of coatings TiN-Cu phases contain-ing various amount of copper. The average size of tita-nium nitride crystallites, estimated according to dark-field images of coating structure and the images of separate particles received with use of TEM, varies from 20 to 100 nanometers in case of copper amount reduction from 20 to 0 at.  (pure titanium nitride) (Fig. 4). Comparison of their sizes with sizes of development shows that nitride phase grains are fragmented by low-angle borders on subgrains. Coatings consist of crystal-lites accidentally oriented relative to each other. The evidence of this are strongly marked rings on electron-diffraction photograph (Fig. 3e). Absence of noticeable nitride phase texture is also supported by data of the X-ray diffraction analysis which speaks for bigger intensi-ty of x-ray diffraction line TiN (200) in relation to (111). Reduction of the nitride phase crystallites size with increase in copper concentration gives evidence of its damming effect on growth process of TiN grains. However, as it is seen from the diagram (Fig. 4), with increase of Cu concentration more than 7−10 at.  of noticeable coating structure refinement does not happen. This fact testifies that this very amount of copper provides complete covering of titanium nitride growing grains and its (copper) further introduction in a coating for the purpose of nitride phase structure refinement makes no sense. This conclusion is also proved by results of created layers hardness measurement. Its average size on 12 measured values decreased from 46−49 to 14−15 hPa for the coatings containing from 3.5 to 20 at. copper , respectively. It can mean that while increasing the copper amount in the coating more important for this characteristic is not the decreasing crystallites size, but the growing amount in a composite of soft plastic met-al. Reduction in hardness of made coating can have a negative impact on its wear resistance. To assess copper impact on titanium nitride coating operability one should take into account not only its modifying influence on coating structure, but also that it increasingly impacts coating heat conductivity. In-crease of copper concentration increases the heat-removal from contact zone of tool nose with work mate-rial that leads to temperature reduction in the cutting zone. The performed analysis of TiN-Cu coatings heat conductivity ( ) by Kurnakov's [8] rule (connecting composite characteristics with components characteris-tics through their weight concentration), shows that λ for the nitride coating containing 20 at.  copper, in-creases to 116 W/(m*K) in comparison with 37 W/(m*К) - value, characteristic for TiN (  for coating TiN-7 at.  of Cu is estimated by 65 W/(m*К). Besides, soft plastic copper influences tribological properties of composite coating, in particular, reduces frictional coefficient by reducing friction force (Fig. 6). a b c  DISCRETE MODIFIED NANOSTRUCTURAL WEARPROOF … PROC. NAP 2, 02FNC07 (2013)   02FNC07-3           Fig. 3 – Electron microscope images of coatings Ti-Cu-N  structure with copper: a, b, c)-20 at. % ; d, e, f)-7at. % ; а, d)- dark-field image; b, e)- bright-field image; c, f)- high-resolution images; g)-  coatings electron-diffraction photograph    Fig. 4 – Dependence of TiN crystallites size in TiN-Cu coating from copper amount  The most important characteristic of any coating is its adhesive and cohesive durability in system "coating -substrate" which we investigated using measuring scratching method. Results of FF, μ, AE, h measurements characteristic for the received coatings are given in Figure 7. Change from the interlocking contact to continuous when the indentor is sliding on a coating surface, if having Lc1 at about 10 H, leads to separation of microparticles from the scratch edges. This process of separation is accom-panied by sharp increase of AE level. It is proved by the optical image of coating damage area (Fig. 8). In pro-cess of load rise the coating has an intensive cohesive destruction which is expressed by formation of     Fig. 6 – Experimental dependences of friction coefficient of friction on rubbing path for samples: 1) firm alloy VK-6; 2) firm alloy VK-6 with TiN coating – 3,5 at. Cu ; 3) firm alloy VK-6 with TiN coating – 7 at. Cu   diagonal cracks set at the bottom of scratch, and also by coating fragmentation without its detachment from a substrate. In process of coating gradual wearing off, the friction coefficient increases a little, and in case of Lc3 loading  55 N we can see its sharp growth. It is connected with covering full destruction and achieve-ment by an indentor the material of substrate. at, %Cu Grain size, nm Constant of friction The path of friction, m a b cc d e f  D.S. BELOV, I.V.BLINKOV, А.О. VOLKHONSKY, J. MIKHALSKY PROC. NAP 2, 02FNC07 (2013)   02FNC07-4   Fig. 7 – Results of measuring scratching of coating Ti-Cu-N with copper amount 9 at.  which has been carried out for studying of adhesive/cohesive durability: curves of h (1), АЕ (2),  (3), FF(4) from applied load to the indentor and scratch length        Fig. 8 – Image of scratch on the coating surface Ti-Cu-N с with copper amount 9 at.% with applied to the indentor loads: 0,9 N(а); 7 N (b); 9,3 N (c); 19 N (d); 29,7 N (e); 52,2 N (f); 60 N (g) 4. CONCLUSION  Processes of structure and phase formation in Ti-N-Cu system were studied when forming ceramic-metallic coatings with copper amount from 0 to 20 at. % using ion-plasma vacuum-arc deposition method. These pro-cesses speak for availability in nitride coating titanium and copper, which before the moment of its concentra-tion in a coating at the amount of 10 at. % is in X-ray amorphous condition. Copper introduction in the coating structure leads to crystallites of a nitride phase refinement from 100 to 20 nanometers in case its concentration change within the interval stated above. Coatings hardness thus grows from 20 to 49 hPa in case of copper amount increase in a coating to 3.5 at. %. Further increase of copper amount to 20 at.%, accom-panied by crystallites of nitride phase refinement, is characterized by hardness reduction up to 14−15 hPa which is connected with influence on it soft plastic metal and appearing the porosity in a coating. In the work the assumption was made on the influ-ence on studied coatings wear resistance in comparison with coatings from titanium nitride their increased heat conductivity and improved tribological properties.                 REFERENCES  1. V. Shtansky, S.A. Kulinich, E.A. Levashov, J.J. Moore, Physics of rigid body 45, No. 6, 1122 (2003). 2. I.V. Blinkov, A.O. Volkhonskiy, A.G. Yudin, Physics and chemistry of materials processing 6, 18 (2011). 3. A. Volkhonskiy, I.V. Blinkov, Russ. J. Non-Ferr. Met. 53, No3, 259 (2012). 4. S. Veprek, M.G.J. Veprek-Heijman, P. Karvankova, J. Prochazka, Thin Solid Films 476, 1 (2005). 5. Yu.F. Ivanov, N.N. Koval, O.V. Krysina et al, Surf. Coat. Tech. 207, 430 (2012). 6. P. Patsalas, G. Abadias, G.M. Matenoglou et al, Surf. Coat. Tech. 205, 1324 (2010). 7. I.V. Blinkov, V.N. Ankin, A.O. Volkhonsky, N.A. Sobolev, R.V. Kratokhvil, HEI news. Powder metallurgy and func-tional coatings 1, 44 (2009). 8. G.N. Dulnev, Yu.P. Zarichnyak, Heat conductivity of mix-tures and composite materials (L.: Energy: 1974).  a b c d e f g 

Discrete Modified Nanostructural Wearproof Coatings TiN-Cu

SocioEconomic Challenges Journal (Sumy State University)

PROCEEDINGS OF THE INTERNATIONAL CONFERENCE  
NANOMATERIALS: APPLICATIONS AND PROPERTIES 
Vol. 2 No 2, 02FNC07 (4pp) (2013) 
 
2304-1862/2013/2(2) 02FNC07 (4) 02FNC07-1  2013 Sumy State University 
Discrete Modified Nanostructural Wearproof Coatings TiN-Cu 
 
D.S. Belov1,*, I.V. Blinkov1,†, A.O. Volkhonskiy1,‡, J. Michalski2 
 
1 National University of Science and Technology “MISiS”, Department of functional and high-temperature materi-
als, 4, Leninskiy Ave., 119049 Moscow, Russian Federation 
2 Institute of Precision Mechanic, 3, Duchnicka St., 01-796 Warsaw, Poland 
 
(Received 20 May 2013; revised manuscript received 05 June 2013; published online 31 August 2013) 
 
Discrete modified nanostructural wearproof coatings Ti-N-Cu with crystallites size from 100 to 20 na-
nometers formed with ion-plasma vacuum-arc method. Copper amount in the received coatings made from 
0 to 20 at. %, their hardness have considerably increased up to about 40-45 hPa in comparison with 20-
22 hPa for Ti-N coverings. In this work, processes of structure and phase formation of Ti-N-Cu system 
coatings in a wide interval of copper concentration are investigated. 
 
Keywords: Wearproof coating, Titanium nitride, Copper, Nanostructuring, Hardness, PVD method, 
Nanoindentation. 
 
 PACS numbers: 68.37. – d, 68.37.Hk, 68.55.Nq. 
 
                                                          
*
 LightningN4S@yandex.ru 
†
 biv@misis.ru 
‡
 abwest@yandex.ru 
1. INTRODUCTION 
 
Nanostructuring of nitride coatings (their prepara-
tion with a size of grains less than 100 nanometers) of 
various functional purpose makes it possible to imple-
ment in them high values of hardness combining with 
plasticity. This thereby provides the added performance 
of wear resistance in conditions of both constant, and 
fatigue loads [1, 2, 3]. 
One of the possible ways to limit growth of coating 
material grains during its deposition is implementation 
to the forming coating the components which will be 
spread over the surface of main coating phase nucleus 
and limit their growth [4, 5, 6]. The main criteria for 
choosing these modifying agents are lack of noticeable 
dissolution in a nitride phase and tendency to nitride 
formation. 
This work includes researches on studying of struc-
ture and properties of TiN-Cu coatings with copper 
wide concentration range received by a method of ion-
plasma vacuum-arc deposition on the hard-alloy cut-
ting tool TT10K8B, including its tests for firmness 
conducted when cutting. 
 
2. RESEARCH TECHNIQUE 
 
Coatings were overlied on an ion-plasma vacuum-
arc unit of Bulat type, including three evaporative 
cathodes with separators of a drop phase in the atmos-
phere of reaction gas nitrogen (PN2  3 10-3 Pa). Cath-
odes from VT-5 alloy, copper and combined from VT-5 
alloy with insertion from Cu were used. The current of 
evaporative arc (Id) was 120 A, the negative bias (Uc) 
energized to the substrate, changed from -80 V to – 
140 V. 
Time of coating sputtering was about 90 minutes, 
their thickness was within 3.9−4.1 micrometers. 
Morphology, structure of coatings was studied using 
a field raster electron microscope JSM-6700F with an 
add-on for energy-dispersive spectrometry JED-2300F, 
JEOL.  
To determine phase composition of a coating the 
imaging with DRON-4 diffractometer was carried out 
using СоКα emission and the graphite monochromator 
on the diffracted beam in asymmetric geometry (the 
angle between the incident ray and sample surface 
being   5º).  
To carry out structural surveys of coatings the 
transmission electron microscope JEM 2100 of high 
resolution, JEOL, Japan was applied.  
For sample thinning ion etching was used.  Ion 
etching was carried out by means of the PIPS equip-
ment (Precision Ion Polishing System, Gatan).  
Coatings hardness (H) and elastic modulus (E) were 
measured by the method of continuous indentation at 
light loads. This test was performed using microiden-
tometer Micro-Hardness Tester (CSM Instruments) 
with fixed loading 300 mN. Indetor penetration depth 
was controlled so that it did not exceed 10  of coating 
thickness to restrict substrate material influence. 
 
3. RESULTS AND THEIR DISCUSSION 
 
Appearance of the created coatings does not differ 
from appearance of the ion-plasma coatings which does 
not contain metal phase [7]. They have a cell structure 
with roughness (Ra) of about 0.3-0.2 microns (Fig. 1). 
Coatings containing 20 at.  of copper have rather 
porous structure which density increases with reduc-
tion in copper amount. 
Copper amount at fixed Id values  120 A and 
Uc  – 120 V varied in a coating from 0.6 to 20 at.  
when using the respective cathodes, due to area ratio 
change of evaporating cathodes coatings - VT-5 and 
copper alloy from 5 to 1. Uc growth from-80 to-140 V, 
(bringing to energy increase of the sprayed ions bom-
barding the substrate) when preserving the identical 
area ratio of cathode surfaces from VT-5 and Cu (2.4), 
and also current of evaporating them electric arches 
 D.S. BELOV, I.V.BLINKOV, А.О. VOLKHONSKY, J. MIKHALSKY PROC. NAP 2, 02FNC07 (2013) 
 
 
02FNC07-2 
(120A) led to reduction of copper amount in a coating 
from 9 to 1.7 at.  in case of its regular distribution on 
all substrate surface. Thus nitrogen amount in a coat-
ing in relation to a nitride composing element – titan - 
also decreased (from 0.91 to 0.86). The increase in non-
stoichiometry TiN is also supported by the lattice con-
stant equal to 4.239 and 4.207 Ǻ respectively for the 
coatings received at Us-80 and – 140 B. This effect is 
connected with preferable spraying from a coating both 
the easiest element - nitrogen, and the copper, which 
bond energy is less than bond energy of titan in nitride. 
 
 
 
Fig. 1 – External appearance of Ti-Cu-N coatings with copper: а) 20 at. %; b) 9 at. %; c) 3 at. % 
 
The x-ray phase analysis speaks for availability in 
all the samples the titanium nitride and copper if its 
amount in the coating is from 20 to 9 at. . In case of 
smaller copper amounts, the lines of its x-ray diffrac-
tion are absent on roentgenograms. The level of nitride 
phase microdeformations of a coating because of copper 
amount (Figure 2) varied from 0.5 to 1.08 . 
 
 
 
Fig. 2 – Change of microdeformations TiN level in TiN–Cu 
coating depending on copper amount 
 
Reduction of their values with increase of copper 
amount in a coating can be connected with relaxed 
influence on them by plastic metal phase. Sizes of the 
stretching macrostresses in the received coatings, de-
termined by the sin2  method, made from 60  40 to 
90  40 MPa that speaks for absence of stress in them. 
The sizes of composite nitride phase development are of 
about 15 nanometers and very little depend on coating 
copper amount. 
In Figure 3, you see the images received by TEM 
method, crystallites of coatings TiN-Cu phases contain-
ing various amount of copper. The average size of tita-
nium nitride crystallites, estimated according to dark-
field images of coating structure and the images of 
separate particles received with use of TEM, varies 
from 20 to 100 nanometers in case of copper amount 
reduction from 20 to 0 at.  (pure titanium nitride) (Fig. 
4). Comparison of their sizes with sizes of development 
shows that nitride phase grains are fragmented by low-
angle borders on subgrains. Coatings consist of crystal-
lites accidentally oriented relative to each other. The 
evidence of this are strongly marked rings on electron-
diffraction photograph (Fig. 3e). Absence of noticeable 
nitride phase texture is also supported by data of the X-
ray diffraction analysis which speaks for bigger intensi-
ty of x-ray diffraction line TiN (200) in relation to (111). 
Reduction of the nitride phase crystallites size with 
increase in copper concentration gives evidence of its 
damming effect on growth process of TiN grains. 
However, as it is seen from the diagram (Fig. 4), 
with increase of Cu concentration more than 7−10 at.  
of noticeable coating structure refinement does not 
happen. This fact testifies that this very amount of 
copper provides complete covering of titanium nitride 
growing grains and its (copper) further introduction in 
a coating for the purpose of nitride phase structure 
refinement makes no sense. 
This conclusion is also proved by results of created 
layers hardness measurement. Its average size on 12 
measured values decreased from 46−49 to 14−15 hPa 
for the coatings containing from 3.5 to 20 at. copper , 
respectively. It can mean that while increasing the 
copper amount in the coating more important for this 
characteristic is not the decreasing crystallites size, but 
the growing amount in a composite of soft plastic met-
al. Reduction in hardness of made coating can have a 
negative impact on its wear resistance. 
To assess copper impact on titanium nitride coating 
operability one should take into account not only its 
modifying influence on coating structure, but also that 
it increasingly impacts coating heat conductivity. In-
crease of copper concentration increases the heat-
removal from contact zone of tool nose with work mate-
rial that leads to temperature reduction in the cutting 
zone. The performed analysis of TiN-Cu coatings heat 
conductivity ( ) by Kurnakov's [8] rule (connecting 
composite characteristics with components characteris-
tics through their weight concentration), shows that λ 
for the nitride coating containing 20 at.  copper, in-
creases to 116 W/(m*K) in comparison with 37 W/(m*К) 
- value, characteristic for TiN (  for coating TiN-7 at.  
of Cu is estimated by 65 W/(m*К). 
Besides, soft plastic copper influences tribological 
properties of composite coating, in particular, reduces 
frictional coefficient by reducing friction force (Fig. 6). 
a b c 
 DISCRETE MODIFIED NANOSTRUCTURAL WEARPROOF … PROC. NAP 2, 02FNC07 (2013) 
 
 
02FNC07-3 
   
 
   
 
 
 
Fig. 3 – Electron microscope images of coatings Ti-Cu-N  structure with copper: a, b, c)-20 at. % ; d, e, f)-7at. % ; а, d)- dark-field 
image; b, e)- bright-field image; c, f)- high-resolution images; g)-  coatings electron-diffraction photograph 
 
 
 
Fig. 4 – Dependence of TiN crystallites size in TiN-Cu coating 
from copper amount 
 
The most important characteristic of any coating is 
its adhesive and cohesive durability in system "coating 
-substrate" which we investigated using measuring 
scratching method. 
Results of FF, μ, AE, h measurements characteristic 
for the received coatings are given in Figure 7. Change 
from the interlocking contact to continuous when the 
indentor is sliding on a coating surface, if having Lc1 at 
about 10 H, leads to separation of microparticles from 
the scratch edges. This process of separation is accom-
panied by sharp increase of AE level. It is proved by the 
optical image of coating damage area (Fig. 8). In pro-
cess of load rise the coating has an intensive cohesive 
destruction which is expressed by formation of  
 
 
 
Fig. 6 – Experimental dependences of friction coefficient of 
friction on rubbing path for samples: 1) firm alloy VK-6; 2) 
firm alloy VK-6 with TiN coating – 3,5 at. Cu ; 3) firm alloy 
VK-6 with TiN coating – 7 at. Cu  
 
diagonal cracks set at the bottom of scratch, and also 
by coating fragmentation without its detachment from 
a substrate. In process of coating gradual wearing off, 
the friction coefficient increases a little, and in case of 
Lc3 loading  55 N we can see its sharp growth. It is 
connected with covering full destruction and achieve-
ment by an indentor the material of substrate. 
at, %Cu 
G
ra
in
 s
iz
e
, 
n
m
 
C
o
n
st
a
n
t 
o
f 
fr
ic
ti
o
n
 
The path of friction, m 
a b c
c d e 
f 
 D.S. BELOV, I.V.BLINKOV, А.О. VOLKHONSKY, J. MIKHALSKY PROC. NAP 2, 02FNC07 (2013) 
 
 
02FNC07-4 
 
 
Fig. 7 – Results of measuring scratching of coating Ti-Cu-N 
with copper amount 9 at.  which has been carried out for 
studying of adhesive/cohesive durability: curves of h (1), АЕ 
(2),  (3), FF(4) from applied load to the indentor and scratch 
length 
 
 
 
 
 
 
 
Fig. 8 – Image of scratch on the coating surface Ti-Cu-N с with 
copper amount 9 at.% with applied to the indentor loads: 0,9 
N(а); 7 N (b); 9,3 N (c); 19 N (d); 29,7 N (e); 52,2 N (f); 60 N (g) 
4. CONCLUSION 
 
Processes of structure and phase formation in Ti-N-
Cu system were studied when forming ceramic-metallic 
coatings with copper amount from 0 to 20 at. % using 
ion-plasma vacuum-arc deposition method. These pro-
cesses speak for availability in nitride coating titanium 
and copper, which before the moment of its concentra-
tion in a coating at the amount of 10 at. % is in X-ray 
amorphous condition. 
Copper introduction in the coating structure leads 
to crystallites of a nitride phase refinement from 100 to 
20 nanometers in case its concentration change within 
the interval stated above. 
Coatings hardness thus grows from 20 to 49 hPa in 
case of copper amount increase in a coating to 3.5 at. %. 
Further increase of copper amount to 20 at.%, accom-
panied by crystallites of nitride phase refinement, is 
characterized by hardness reduction up to 14−15 hPa 
which is connected with influence on it soft plastic 
metal and appearing the porosity in a coating. 
In the work the assumption was made on the influ-
ence on studied coatings wear resistance in comparison 
with coatings from titanium nitride their increased 
heat conductivity and improved tribological properties. 
 
 
 
 
 
 
 
 
 
 
 
 
 
 
 
 
REFERENCES 
 
1. V. Shtansky, S.A. Kulinich, E.A. Levashov, J.J. Moore, 
Physics of rigid body 45, No. 6, 1122 (2003). 
2. I.V. Blinkov, A.O. Volkhonskiy, A.G. Yudin, Physics and 
chemistry of materials processing 6, 18 (2011). 
3. A. Volkhonskiy, I.V. Blinkov, Russ. J. Non-Ferr. Met. 53, 
No3, 259 (2012). 
4. S. Veprek, M.G.J. Veprek-Heijman, P. Karvankova, 
J. Prochazka, Thin Solid Films 476, 1 (2005). 
5. Yu.F. Ivanov, N.N. Koval, O.V. Krysina et al, Surf. Coat. 
Tech. 207, 430 (2012). 
6. P. Patsalas, G. Abadias, G.M. Matenoglou et al, Surf. 
Coat. Tech. 205, 1324 (2010). 
7. I.V. Blinkov, V.N. Ankin, A.O. Volkhonsky, N.A. Sobolev, 
R.V. Kratokhvil, HEI news. Powder metallurgy and func-
tional coatings 1, 44 (2009). 
8. G.N. Dulnev, Yu.P. Zarichnyak, Heat conductivity of mix-
tures and composite materials (L.: Energy: 1974). 
 
a b c 
d e f 
g 


https://essuir.sumdu.edu.ua/bitstream/123456789/35311/1/princon_2013_2_2_55.pdf

Discrete Modified Nanostructural Wearproof Coatings TiN-Cu

Abstract

Similar works

Full text

Available Versions

Electronic Sumy State University Institutional Repository

SocioEconomic Challenges Journal (Sumy State University)