Sintering Behavior and Properties of cBN/TiC/ SWCNTs or NC Ceramics Matrix Nanocomposites (CMNC’s) by Field Actived Sparck Plasma Sinter

Cubic boron nitrid (cBN) bonded TiC and alloyed with single walled carbon nanotubes (SWCNTs or NC) ceramics matrix nanocomposites (CMNC’s) tools were fabricated by a field active sparck plasma sintering process (FASPS). The effects of cBN-TiC ratio, carbon nanotubes and optimization of the sintering process on the microstructure, densification in addition mechanical and vibronic properties of NC-cBN-TiC nanocomposites were studied. The results showed that the nanocomposite cBN-TiC vol. ratio of 8:2 with 0.1 wt% NC. It was found that microhardness increases significantly with addition of NC exhibited the highest microhardness and fracture toughness. After sinters of the samples at 1800°C, 10 mn, 75 MPa of cBN–TiC1-x with x=0.8 with and without addition of 0.1 wt% NC were characterized using field emission scanning electron microscopy (FESEM) and X-ray diffraction. The samples exhibited a dense polycrystalline structure, from the resonant Raman scattering we can locate the vibration frequency of the transformation cBN to hexagonal boron nitrid (hBN) and formation of secondary hard phase TiB2 to consoled the (CMNC’s) tools. The final product is hBN-TiC-TiB2-NC.The best product contained cBNx-TiC1-x (x=0.8)-0.1 wt% NC which was sintered at 1800°C, 75 MPa for 10 mn. The Vickers hardness of cBN-TiC1-x (x=0.8) increases with NC incorporation in the matrix The indentation fracture toughness was calculated to be 12.30 MPa m for cBNx-TiC1-x (x=0.8)-0.1 wt% NC ceramics matrix nanocomposite (CMNC’s) tools with excellent wear resistant will be confirmed. The wear of cBN-TiC of the composites tools have shown that this is predominantly a chemical process involving the interaction of the tool with its environment and is restricted by the formation of protective layers on the exposed faces of the tool by the addition of NC. The wear features of tools used in fine cutting tests under identical conditions will be compared and the results will be interpreted in terms of the existing models for the wear of cBN-based nanomaterials by the effects of the additives in the modified tools.


Abstract Cubic boron nitrid (cBN) bonded TiC and
alloyed with single walled carbon nanotubes (SWCNTs or NC) ceramics matrix nanocomposites (CMNC's) tools were fabricated by a field active sparck plasma sintering process (FASPS). The effects of cBN-TiC ratio, carbon nanotubes and optimization of the sintering process on the microstructure, densification in addition mechanical and vibronic properties of NC-cBN-TiC nanocomposites were studied. The results showed that the nanocomposite cBN-TiC vol. ratio of 8:2 with 0.1 wt% NC. It was found that microhardness increases significantly with addition of NC exhibited the highest microhardness and fracture toughness. After sinters of the samples at 1800°C, 10 mn, 75 MPa of cBN-TiC 1-x with x=0.8 with and without addition of 0.1 wt% NC were characterized using field emission scanning electron microscopy (FESEM) and X-ray diffraction. The samples exhibited a dense polycrystalline structure, from the resonant Raman scattering we can locate the vibration frequency of the transformation cBN to hexagonal boron nitrid (hBN) and formation of secondary hard phase TiB 2 to consoled the (CMNC's) tools. The final product is hBN-TiC-TiB 2 -NC.The best product contained cBN x -TiC 1-x (x=0.8)-0.1 wt% NC which was sintered at 1800°C, 75 MPa for 10 mn. The Vickers hardness of cBN-TiC 1-x (x=0.8) increases with NC incorporation in the matrix The indentation fracture toughness was calculated to be 12.30 MPa m 1/2 for cBN x -TiC 1-x (x=0.8)-0.1 wt% NC ceramics matrix nanocomposite (CMNC's) tools with excellent wear resistant will be confirmed. The wear of cBN-TiC of the composites tools have shown that this is predominantly a chemical process involving the interaction of the tool with its environment and is restricted by the formation of protective layers on the exposed faces of the tool by the addition of NC. The wear features of tools used in fine cutting tests under identical conditions will be compared and the results will be interpreted in terms of the existing models for the wear of cBN-based nanomaterials by the effects of the additives in the modified tools.

Introduction
BN in the cubic super hard modification is a promising material in both bulk and thin film applications is the second hardest material after diamond, and possesses due to its hardness, its high electrical resistivity in combination with high thermal shock behavior, high corrosion resistance, and high transparency for x-rays. Numerous excellent physical and chemical properties, high resistance to chemical attack, and mechanical properties are presented [1][2][3]. The properties such as high thermal and chemical stability exhibited in [4][5][6][7]. High hardness, fracture toughness, wear resistance and low coefficient of friction are the basic materials characteristics most desired for advanced ceramic composites, especially for cutting tools applications The brittleness and poor damage tolerance have limited their application as advanced engineering materials particularly for cutting applications so far [1].
A wide range of various ceramic matrix composites (CMC's), reinforced by addition of titanium carbide (TiC), silicon carbide (SiC), titanium diboride (TiB 2 ) and other hard particles to Al 2 O 3 matrix, were investigated to improve mechanical properties of based materials. The composites were fabricated mainly with the pressure assisted methods (e.g. hot-pressing). In most cases the significant enhancement in hardness, fracture toughness or/and the wear properties was achieved [1][2][3][8][9][10].
In composites with high cubic boron nitride content, the bonding phase only activates the sintering process and fills the gaps between cBN grains and thereby increases the fracture toughness but does not significantly influence other properties of the composite, which are determined by the cBN phase. The control of thermal and chemical properties of the composite relies on the content of the bonding phase, which needs to be relatively high. Therefore, composites consisting of relatively low content of cBN grains are frequently used for high speed machining, where the temperature at the cutting edge can reach 1000 • C and high thermal and chemical resistance of the tools is more important than its mechanical strength. PCD are among the most expensive tool materials because diamond and cBN phases are metastable and for their processing the high pressure-high temperature (HPHT) conditions are required [5][6][7][11][12][13]. When compared to diamond, cBN is particularly attractive due to its superior fracture toughness and oxidation resistance. cBN form was used to produce composite materials [1][2][3][4][5][8][9][10][11][12]. Owing to their unique physico-mechanical properties, these materials are frequently used in machine engineering as cutting blades which are especially useful for processing quenched steel and cast iron. As a binding phase, composite metals of the elements in groups IV-VI of the periodic table, or their compounds, are most frequently used. Among the binding phases, TiN, TiC and TiB 2 exhibit the highest chemical activity towards BN [1][2][3][4][5][6][7][8][9][10][8][9][10][11][12][13][14][15]. The aim of this work was to study chemical equilibria, morphology and mechanical properties in the cBN-TiC and cBN-TiC-TiB 2 -NC nanocomposites systems.
When compared to diamond, cBN is particularly attractive due to its superior fracture toughness and oxidation resistance. cBN was used to produce composite materials [1][2][3][4][5][16][17][18][19][20]. Owing to their unique physico-mechanical properties, these materials are frequently used in machine engineering as cutting blades which are especially useful for processing quenched steel and cast iron. As a binding phase, composite metals of the elements in groups IV-VI of the periodic table, or their compounds, are most frequently used. Among the binding phases, TiN and TiC exhibit the highest chemical activity towards BN [1][2][3][4][5][6][7][8][9][10][16][17][18][19][20][21][22][23][24]. The aim of present work was to study chemical equilibria, morphology and mechanical strength in the cBN-TiN and cBN -TiC systems. There are no studies available in literature that addresses the usage of another hard phase matrix instead of NC, which carries out cutting procedure in nanocomposites cBN-TiC-NC excepted cBN-Diamond cutting tools BN [25].The aim of this work was to investigate the effect NC content on the ceramics matrix nanocomposites (CMNCs) tools cBN-TiC-NC and sintering behaviour on the Vickers microhardness and fracture toughness of cBN-TiC-NC cutting tools produced by FASPS. Major amounts of cBN were added to the segment matrix. FASPS process was carried out at 75 MPa pressure, at T=1800°C. A field emission scanning electron microscope (FESEM) and an X ray diffractometer (XRD) were used to analyze the microstructure, chemical compound, and fracture surfaces of each segment type, in addition mechanical and vibronic properties by Vickers microhardness, fracture toughness (K IC ) and Raman spectroscopy are performed on the nanocomposites to evaluate the effect of the NC additive phase on the performance of the catting tools.
The wear features of tools used in fine cutting tests under identical conditions will be compared and the results will be interpreted in terms of the existing models for the wear of cBN -based nanomaterials by the effects of the additives in the modified tools.

Experimental Procedure
Commercially available ultra-fine powder of TiC (<3 µm, 99.8% purity, Sumitomo Sitix, Co. Ltd., Japan, cBN (<5 µm, 99.8% purity, Nihon New Metals Co. Ltd., Japan) and NC produced by HIPCO process with diameter of 1.0 nm (IFW-TU-Dresden-Germany) were used as the reinforcement materials. The mixture containing cBN x -TiC 1-x (x=0.8) and with addition of 0.1 wt% of NC nanocomposites were prepared by wet milling in anhydrous alcohol for 3 h. To obtain homogenized and fine powder mixtures, the powder mixtures of cBN-TiC were ball-milled at a high speed of 200 RPM for 12 h by using WC balls (diameter: 3 mm) and ethanol as the milling media. Preliminary treatment of NC was carried out to minimize the agglomerate of the added NC. Firstly; the weighed NC were immersed into acetone for about 20 h, and then were ultrasonically dispersed for 4 h. Secondly, the treated NC (3 vol.%) were mixed with the former ball-milled blend (cBN x -TiC 1-x (x=0.8) by magnetic agitation for 8 h. Again, a ball milling was applied to the slurry cBN x -TiC 1-x (x=0.8) at a speed of 250 RPM for 08 h for further mixing. Finally, the powder mixtures with dispersed NC were dried by rotary evaporator under vacuum condition and were sieved to 70 meshes. Based on previous sintering tests, the composition ratio of the nanocomposites was designed as follows (vol. %): cBN x -TiC 1-x (x=0.8)-0.1wt%. NC (here after, it is referred as BTNC). The nanocomposites were sintered by FASPS technology. The two sintering schedules are shown in Fig.1. In the sparck plasma sintering process, temperature profile and die displacement or shrinkage the displacement velocity and puissance power is not presented here (Fig.1). The resulting BTNC ultrafine powder mixtures were hot-pressed in graphite dies (inner diameter of 20 mm) coated with graphite shit lubricant at 1800°C in vacuum. The applied pressure of 75 MPa was adjusted to the powder at room temperature and kept constant throughout the hot pressing process. The pressure was applied at the beginning of the sintering process because high green density is favorable for better densification rate by reducing the pores prior to the densification during heating. The heating rate was about 10°C/min and the dwelling time at terminal temperature was 60 min. The temperature was measured by an infrared pyrometer through a hole opened in the graphite die. Furthermore, for monitoring densification process, the shrinkage of the powder compact was measured by a displacement sensor during the hot pressing.
The dimensions of the finally hot pressed samples were about 20 mm in diameter and 3 mm in thickness.
The mixtures were loosely compacted into a graphite die of 20 mm in diameter and sintered in the vacuum (1 Pa) at various temperatures (1800°C) using an FASPS apparatus (Lab. Sinter, FASPS-1050, Sumitomo Coal Mining Co. Ltd., Germany) ( Table 1). A constant heating rate of 120°C/min was employed, while the applied pressure was 75 MPa. The on/off time ratio of the pulsed current was set to 10/2 in each run. The maximum current reached approximately 3000 A during sintering. The soaking time at high temperatures was within 10 mn. The upper ram of the FASPS apparatus was fixed, while the displacement of the shifting lower press ram was recorded in order to analyze the synthesis and sintering. The sintered samples are presented in the Fig.2.  Sintering Behavior and Properties of cBN/TiC/ SWCNTs or NC Ceramics Matrix Nanocomposites (CMNC's) by Field Actived Sparck Plasma Sinter Density of the sintered samples was measured by the Archimede's using the densimeter type Micromiritics Accupyc 1330. The microhardness at the top was measured by a diamond Vickers hardness tester (MVK-H1, Meter-Mitutoyo, Japan).
The indentation loads, ranging from 10 to 500 N, were applied for 15 s for each measurement. The fracture toughness was measured using the Vickers indentation by the measurements of the producing failler.
In this study, 06 samples for each sintering process were fabricated to obtain an average relative density and hardness.
Young's modulus of the composites was determined by ultrasonic wave transition method measuring the velocity of ultrasonic sound waves passing through the material using an ultrasonic flaw detector (Panametrics Epoch III). The hardness and the fracture toughness were determined by the Vickers indentation method applying load of 294 N (HV 30 ) and 490 N (HV 50 ), by a Future Tech FLC-50VX hardness tester. For each sample 6 indentations were made and the stress intensity factor K IC was calculated from the length of Palmqvist cracks which developed during a Vickers indentation test using E. Rocha-Rangel's equation [29]. The wear resistance and the friction coefficient will be performed in the near future. The hardness (H), the elastic modulus (E) and the toughness (K IC ) of the fabricated samples were measured under ambient conditions using the instrumented Vickers indentation method (Zwick Roell, ZHU 2.5 apparatus).
The impression diagonal (2a) was measured, and the hardness values were calculated according to the following relation: 2 (1) The fracture toughness was also calculated by indentation fracture (IF) method according to the equation: Where H v was the Vickers hardness, a was the half-length of the indentation diagonal and c was the half-length of the median crack generated by indentation. Generally, the fracture toughness measured by IF method were fluctuating values with relatively large deviations due to the phase distribution and measurement errors of calculation. Thus a linear regression model was applied to get a reliable value of indentation fracture toughness.
To obtain the values of A, B and R 2 , a series of indentation loads (10 N, 50 N, 100 N, 300, 500 N) were applied to get the relations of P and c 3/2 Where P was the indentation load, through the combination of equations (1) and (2), the linear relation between P and c 3/2 was obtained: P = Ac 3/2 +B (A= K IC / 0.075) A linear regression analysis was applied to the relations of P and c 3/2 by the least square method, where A was the slope, B was the intercept, to obtain the values of A and B.
In addition, a high determination coefficient (R 2 ) was obtained through the linear regression model. Hence, when combined with the linear regression model, IF was shown to be an effective method in the evaluation of fracture toughness for its convenience and material saving [30].

Results and Discussion
In this research, significant progress has been made in: (1) FASPS synthesis of cBN powder (2)  The sample is already fully densified to 98% at T= 1800°C at the beginning of the heating with a fast displacement of the dies and remains until the end of the heating, the temperature sensor records the displacement of the dies from T= 400°C (pyrometer). The NC enhanced sample has better sintering behavior and densification than NC free. Fig. 1 shows also the thermodilatometric measurements up to 1800°C under vacuum in the FASPS chamber for different compositions. This experiment was performed in order to optimize the sintering temperature. As can be seen on the graph, the starting shrinkage temperature slightly increases with addition of the NC. At T= 400°C we beginning the measurements. We will compare the dilatometric curves versus-heating time with versus temperature in the future experiments.

XRD Analysis of Sintered cBN x -TiC 1-x (x=0.8) -0.1 wt% NC (CMNC's) Tools
In all two samples, XRD analysis shows that the crystallite size of the consolidated material is ~26 nm, which is about one-half the initial grain size (~56 nm) of powder. All samples are analyzed by XRD (Fig.3), and where appropriate by FESEM. The standard XRD spectra for several phases of interest herein for the reference purpose [26]. The Bravais structure of cBN, hBN, TiC, bundles of NC and TiB 2 are illustrated in the Fig.4    XRD analysis of the samples indicates that the only phases formed in the sample without NC are titanium carbide TiC (5 µm), with a cubic crystal structure and the transformation of the cBN to hBN crystal structure. The addition of 0.1 wt% NC has considerable effect on XRD pattern. (intensity of the XRD spectrum of the nanocomposite, which indicates that the reaction between the TiC, cBN powders and NC did happen during the sintering process in the system cBN-TiC-NC. The X-ray diffraction investigations were carried out with diffractometer (Philips 1710) using CoK α radiation. The X-ray diffraction phase analysis and profile of diffraction line analysis were applied. After sintering of the investigated samples the following new phases (Fig.3) were formed TiB 2 in the cBN-TiC system, and TiB 2 in cBN x -TiC 1-x (x=0.8)-0.1 wt% NC ceramics matrix nanocomposite (CMNC's) tools systems. The shape of diffraction lines is a powerful tool for fine microstructure characterization. The line half-width contains information about average crystalline size and lattice defect density which can be treated as internal stored energy [27]. When we compare the intensities of the tree pics located at 32, 42.5 and 50 degrees corresponding to TiB 2 , TiC and cBN to hBN, respectively. The highest intensity is observed for the TiB 2 phase when the samples is reinforced by NC (graphitic pic located at 26 degrees) (Fig.3a and  Fig.3b).The addition of NC by 0.1 wt% move the reaction of more boron atomes to react with TiC and produced TiB 2 phase for additional consolidation of the (CMNC's) tools.
A possible explanation is that densification via plastic deformation under high pressure is incomplete, forming micro-pores at "triple junctions" between cBN grains, which then become favorable sites for nucleation and growth of the lower density hBN. Such behavior is most likely to occur during heat -up of the sample under high pressure. The larger amount of hBN in the sample processed at 75 MPa may be attributed to the same cause. Because of the reduced pressure, densification via plastic deformation is less complete, leaving larger micro-pores at triple junctions of cBN that allow more hBN to form. Plastic deformation accompanied by recrystallization at points of contact between neighboring cBN particles under high pressure is a possible explanation.
However, as noted above, fully dense pure phase cBN is not achievable under the designated processing conditions; a small fraction of hBN is invariably formed. To eliminate cBN decomposition during FASPS, it will be necessary to investigate the use of sintering aids. The additions of TiC to cBN prevent its decomposition into hBN, probably by forming a thin surface-passivation film of TiC-base compounds. Moreover, by controlling reactions between TiC and cBN phases, fully dense composite structures can be obtained, comprising high fractions of superhard cBN particles cemented together with hard TiB 2 composites. By the addition of 0.1 wt% of NC we obtain a superhard ceramics matrix nanocomposites (CMNC's) tool. When such composite structures contain residual un-reacted TiC, there is the prospect of enhanced toughness, while retaining high hardness, stiffness. To summarize, fully dense nanocrystalline cBN -TiC can be produced by FASPS processing, but the formation of a minor fraction of hBN seems unavoidable. This is unfortunate, since the presence of even a small amount of hBN, particularly at nano-grain boundaries, must adversely affect fracture toughness. On the other hand, an addition of TiC to cBN provides a route to produce fully 126 Sintering Behavior and Properties of cBN/TiC/ SWCNTs or NC Ceramics Matrix Nanocomposites (CMNC's) by Field Actived Sparck Plasma Sinter dense cBN-based composites with hBN, and thus potentially enhance mechanical performance. The FESEM microstructures of samples with following compositions: The FESEM microstructures (Fig.5) revelated that the ceramics matrix nanocomposites (CMNCs)) tools has good density of the binderless phases in the final structure of the products. The high magnification representative microstructure of the sample without NC (Fig. 5a-b-k-i) consists of large hBN (dark) grains (Fig.5 e-f-h) and TiC (gray) (Fig. 5c-d) particle sintered together and remaining not transformed and unreacted cBN (Fig.5 k-i)The addition of 0.1 wt% N C (Fig.5e-f) to the reaction changed the morphology of hBN from slightly finer grains with near spherical morphology to the large plate like grains. Fig.  5e-d, show the NC intra TiC and hBN particle grain and no in the grain boundaries forming the interface with different orientations. The mechanical properties are induced by both phases and grain boundaries. This contributes to the increasing of the Vickers microhardness. In the Fig.5 k-i is presented the typical of the loss of NC identified by the pore like structure (canneaux). High magnification images of the starting ultrafine powder of NC and sintered titanium carbide (TiC) are presented in Fig. 5a-b and c-d.

wt % NC (CMNC's) Tools
The influence of the addition of the reinfort of carbon nanotubes on the relaties density of sintered cBN x -TiC 1-x (x=0.8) nanocomposites is shown in Table.2. The theoretical density of the nanocomposite used for obtaining relative density was calculated using a rule of mixture, using the densities of two constituents has (ρ hBN= 2.1 g/cm 3 ,ρ cBN = 3.45 g/cm 3 , ρ TiiC = 4.50 g/cm 3 , ρ NC= 2.25 g/cm 3 ) with the given SPS processing parameters, the cBN x -TiC 1-x (x=0.8) with and without 0.1 wt% NC sample exhibited best densification with relative density greater than 97.5%, with the similar processing parameters with addition of carbon nanotubes. The relative density increases with the addition of NC.
The cBN x -TiC 1-x (x=0.8)-0.1 wt% NC nanocomposites at T=1800°C exhibited relative density of about 98.5%. Depending on the final density to be achieved, the FASPS operating condition were properly chosen, that is, 1800°C, 75 MPa for 10 mn, to obtain a highest relative density for the nanocomposites cBN x -TiC 1-x (x=0.8), dense cBN x -TiC 1-x (x=0.8)-0.1 wt% NC, TiC for zero compacts porosity, 97.5, 98.06, and 94.06, respectively. Also, the easy sledding of their walls when attached by weak van der Waals force of coalesced MWCNTs can probably increases the relative density. The density of the sintered samples was determined using the Archimedes helium immersion method.

Vickers Microhardness of Sintered cBN x -TiC 1-x (x=0.8)-0.1 wt% NC (CMNCs) Tools
According to the above results, it can be concluded that the Vickers hardness has been improved by adding NC and enhanced with the fracture toughness value giving a better ductility for the reinforced NC samples. Fig. 8 shows the hardness as a function of the applied indentation load for the same sample. At lower loads, the microhardness reaches a low hardness a constant value of 47.55, 18 and 35.26 GPa at HV 50 for reinforced cBN x -TiC 1-x (x=0.8)-0.1 wt% NC, TiC, and unreinforced cBN x -TiC 1-x (x=0.8), nanocomposites with CN, respectively.
In the present study, the high hardness of the FASPS synthesized sample containing nanocomposite cBN x -TiC 1-x (x=0.8)-0.1 wt% NC at T= 1800 °C may be attributed to its high density (98.5% from theoretical).  (18 GPa). For the nearly single phase hBN sintered (FASPS) in this investigation, the microhardness was found to be 30 GPa (measured with indentation load of 300 N), which is higher than the previously reported hardness values for hexagonal in the literature. While the higher hardness of the cBN x -TiC 1-x (x=0.8)-0.1 wt% NC nanocomposite sample could be due to a minor amount of NC intragranular reinforced TiC grain phase in the nanocompositecBN x -TiC 1-x (x=0.8).
The highest Vickers microhardness in the range of about 55 GPa was found for lower loads (10 N). A slight increase in average hardness have been obtained from nanocomposites prepared by FASPS sintering of cBN x -TiC 1-x (x=0.8)-0.1 wt% NC at T=1800 °C exhibited highest hardness of about 47.55 GPa was found for lower loads (500 N). (Fig.6), It is considered that cBN 20 vol% TiC with the remaining 0.1 wt% NC act as reinforcements play the major role in the consolidation of the products.
With this addition in the matrix, the electro-discharge among powders may lead to self-heating and purification of the particle surface, resulting in activation of the formation of the nanocomposites.

Fracture Toughness (K IC ) of Sintered cBN x -TiC 1-x (x=0.8)-0.1 wt% NC (CMNC's) Tools
The relevant data were listed in Table 3.In Fig. 9, a linear regression analysis was applied to the relations of P and c 3/2 by the least square method.   9. Correlation between the applied load P and half-length of median crack c 3/2 of polished and etched surface for the sintered samples using the (IF) method As a result, the calculated slope A and intercept B were 0.0827 and 4.2534, respectively. The indentation fracture toughness was calculated to be 12.30 MPa m 1/2 for cBN x -TiC 1-x (x=0.8) -0.1 wt% NC ceramics matrix (CMNC's) tools with excellent wear resistant will be confirmed.
The addition of NC plays a important binderless role (the ductility) in the propagation of failler in this nanocomposites and thus enhance the fracture toughness in comparison with his higher hardness In addition, a high determination coefficient (R 2 ) of 0.9961 was obtained through the linear regression model [30]. IF (indentation fracture) was shown to be an effective method in the evaluation of fracture toughness for its convenience and material saving.

Raman Scattering of cBN x -TiC 1-x (x=0.8)-0.1 wt% NC (CMNC's) Tools
In the Fig.10 is presented the Raman response of the nanocomposites cBN x -TiC 1-x (x=0.8)-0.1 wt% NC, TiC and cBN x -TiC 1-x (x=0.8) with laser excited by λ exc =244 nm. The transition of cBN to hBN are detected by the vibration frequency response by tree vibration mode of the hexagonal lattice longitudinal (LO), transversal (TO) and E 2g arround the 1447 for E 2g , 2142 for 2LA(K), 2656 for 2TO(KM) and 2887, 3060 cm -1 for 2LO(T) respectively, according to [28]. The reinforced phase of the binderless NC is localized in the typical frequency of G and D mode at 1351and (1524, 1594) cm -1 , respectively. The Raman spectra confirm the XRD investigations.

Conclusions
We have successful produced (CMNCs)tools by FASPS with several quantities of TiC ultrafine powder were added to the FASPS sintered dense cBN x -TiC 1-x (x=0.8)-0.1 wt% NC (CMNCs) tools at 1800°C under a pressure of 75 MPa for 10 mn in high vacuum protection. Phase analysis using XRD and EDX indicated that binderless fines powders hBN, TiC and TiB 2 and un-reacted binder phase NC and untransformed cBN were the main products. Microstructural observations by FESEM showed that the effect of NC as binder phase make interface intra TiC grains and good physical (relative density) and mechanical properties (Vickers microhardness, yung's modulus, fluxual strain, friction coefficient and fracture toughness) of nanocomposite are obtain for cBN x -TiC 1-x (x=0.8)-0.1 wt % NC, FASPS produced samples .The loss of NC during or conversion of NC the sintering process are illustrated by the pore like structure in the FESEM pictures.
The best density 98.5% from the theoretical and ductility of the nanocomposites ceramics matrix tools cBN x -TiC 1-x (x=0.8)-0.1 wt% NC is obtain with the addition of the binderless reinfort phase NC and 20 vol.% of TiC.
The fracture toughness is enhanced (ductile nanocomposite) K IC =12.24 MPa m 1/2 in comparison with his highest Vickers hardness. The Raman response confirms the XRD investigations of the sintered samples. Furthers measurements will be carried out with the nanoindentation technics.
Furthers studies also will be performed with variation of the graphite die diameter, to control the NC content in the nanocomposites ceramics matrix tools cBN x -TiC 1-x (x=0.8)-0.1 wt% NC. By FASPS, the extensive volume expansion as a function of the pressure will occur. We will be finding efficiency methods for mixing of NC in (CMNC's) tools; NC will be metallized before mixing and sintering for minimizing theirs loss.
For guidance of NC we are planning to install a magnetic field device around the temperature FASPS chamber to give a NC orientation in the matrix to get better properties of manufactured (CMNC's) tools.