**3. Experimental results and analysis**

## **3.1. Metallurgical analysis of carbonitriding fixtures**

By measuring the micro hardness of thermally treated and ion-nitrided samples in depth, the maximum surface hardness - HV0.1 - and the total thickness of the nitrided layer - δtot have been defined; by means of a metallographic microscope the thickness of the combined zone - δсz - has been determined. The results are given in [Table 4].

It can be seen [Table 4] that after nitriding 25GrMnSiNiMo steel and Armco-Fe, under the modes [1, 8 and 4], a nitrided layer with different surface micro hardness, total thickness and combined zone thickness is obtained. Under these three modes of nitriding 25GrMnSiNiMo steel has a higher micro hardness but a lower total thickness of the layer and a thicker combined zone than Armco-Fe. This fact could be explained by the presence of alloying constituents in the steel, which actively participate in forming nitrides and


strengthening the surface layer. They impede the diffusion of the nitrogen in depth, and in consequence, thinner layers with a thicker combined zone are obtained.

118 Heat Treatment – Conventional and Novel Applications

2θ = 156°

30'

and θ = 78°

( ) ( ) 0 90 .cot 2 2 2 1 180

θθ

The values of the elasticity constants in the given formula are chosen for non - carbonitrided steel: Poisson's ratio μ = 0.29, elasticity modulus E = 210 GPA. The master diffraction angle is

= = = − <sup>+</sup>

ψ

 ψ

. The miscount at defining stresses depends on the relative mistake

 θ π

*Е*

**Figure 1.** Characteristics of the direction of measuring by the angles Ψ and φ

By measuring the micro hardness of thermally treated and ion-nitrided samples in depth, the maximum surface hardness - HV0.1 - and the total thickness of the nitrided layer - δtot have been defined; by means of a metallographic microscope the thickness of the combined

It can be seen [Table 4] that after nitriding 25GrMnSiNiMo steel and Armco-Fe, under the modes [1, 8 and 4], a nitrided layer with different surface micro hardness, total thickness and combined zone thickness is obtained. Under these three modes of nitriding 25GrMnSiNiMo steel has a higher micro hardness but a lower total thickness of the layer and a thicker combined zone than Armco-Fe. This fact could be explained by the presence of alloying constituents in the steel, which actively participate in forming nitrides and

**3.1. Metallurgical analysis of carbonitriding fixtures** 

zone - δсz - has been determined. The results are given in [Table 4].

**3. Experimental results and analysis** 

μ

φ

σ

15'

∆θ/θ at defining the angle θ. It is within 2 - 3**%.**

During the process of carbonitriding of 25GrMnSiNiMo steel in a medium, consisting of 90% NH3 + 8.2% Ar + 1.8 % CO2 at the pressure of 400Ра, a layer with a lower micro hardness (HV0.1= 9400 - 8600МРа), total thickness (160 - 290 μm) and combined zone thickness (5 - 8μm) is obtained, than after the process of nitriding without addition of a carbon-containing gas. This is most likely due to the small percentage of argon (8.2%) in the gas medium, since argon, because of its bigger atomic mass, has a strong pulverizing action. At the high coefficient of pulverizing the length of the free run of the pulverized atoms is bigger and the possibility for a backward diffusion of carbon and nitrogen is lower. A carbonitrided layer with a lower concentration of nitrogen and carbon is obtained. The more active pulverization does not allow the combined zone to grow and, as a result, a more deficient in nitrogen and carbon combined zone is obtained. In the diffusion zone of the carbonitrided layer of the steel detectable nitrided (carbonitrided) precipitations are not observed – [Fig.2.a].

After Armco-Fe carbonitriding under the same mode there are no similar dependences established during the process of forming the layer as the ones, described for 25GrMnSiNiMo steel. The obtained carbonitrided layer has a higher surface micro hardness (HV0.1= 4200 – 4300 МРа), total thickness (260-340 μm) and combined zone thickness (6-7 μm). In the diffusion zone of a carbonitrided layer considerable amounts of nitrided (carbonitrided) precipitations are observed, mainly in the area of the grains. The precipitations originate at the boundary of the grains and propagate inward the volume. A bigger amount of precipitations is observed under the longer mode (6h) of carbonitriding – [Fig.2.c].

**Table 4.** Results from carbonitriding and nitriding of 25GrMnSiNiMo steel and Armco-Fe samples

Carbonitriding of Materials in Low Temperature Plasma 121

carbonitriding with 50% NH3 and 50 % carbon [Table 1, modes 5-6, Fig.3]. This is probably due to the diffusion of carbon in the diffusion zone of the carbonitrided layer as well. Together with the increase of the pressure of the gas medium to 700Ра (NH3 - 350 Ра and corgon -350 Ра – [modes 9-10, Table 1] in the process of carbonitriding of the two materials under investigation, layers with essential differences are formed. After 25GrMnSiNiMo steel carbonitriding layers with a lowest surface micro hardness (HV0.1= 7400 - 7500 МРа) and total thickness (140 -230 μm) in comparison to all the other modes of nitriding and carbonitriding are obtained. The white zone is non-uniform and broken – [Fig.4]. This is probably due to the increased amount of argon in the gas medium and the high density of the current at the higher pressure of the gas medium, as well as to the low voltage of the

**Figure 3.** Microstructure of 25GrMnSiNiMo steel [а, b] and Armco-Fe[c] after carbonitriding at: t =

After Armco-Fe carbonitriding under the same modes of treatment a layer with highest micro hardness (HV0.1= 5400-5600 МРа) and lowest combined zone thickness (4 μm) in comparison to all the other modes of nitriding and carboniding is obtained. In the diffusion zone of the carbonitrided layer the smallest amount of precipitations with the smallest sizes

Under the same mode of treatment, 25GrMnSiNiMo steel possesses higher micro hardness and smaller total thickness of the nitrided and carbonitrided layer, than Armco-Fe. After certain treatment of 25GrMnSiNiMo steel with an additionally introduced carboncontaining gas (carbon) in the ammonia medium at different percentage ratios layers with lower depth, surface hardness and combined zone thickness than in the process of nitriding

After conducting the process of carbonitriding of the investigated materials with carbon (82 % Ar + 18 % CO2) and ammonia, layers of small combined zone thickness are obtained. For

550С, Р NH3 = 200Pa, Р 82% Ar +18% CO2 = 200Ра; а, c - τ = 2h, b - τ = 6h

in comparison to all the other modes of carbonitriding is observed.

discharge [380V, Table 4.].

are obtained.

**Figure 2.** Microstructure of 25GrMnSiNiMo steel [a] and Armco-Fe [b, c] after carbonitriding at: t = 550С, Р NH3 = 360Pa, Р 82% Ar +18% CO2 = 40Ра; а, c - τ = 6h, b - τ = 2 h

Together with the increase in the pressure of carbon (Р 82% Ar +18% CO2 = 200Ра, [Table 4] in a gas medium, in case of 25GrMnSiNiMo steel treatment carbonitrided layers are formed, having lower micro hardness (HV0.1= 8900- 9200 МРа), total thickness (150-240 μm) and combined zone thickness (5-8 μm), than under the modes of treatment, considered so far. It is due to the increased activity of pulverizing, since the amount of argon in the gas medium is bigger - 41%. The higher rate of pulverizing leads to decreasing the probability for collisions between the atoms and ions, in consequence of which smaller amount of nitrogen and carbon is delivered to the surface. The microstructure analysis of the layer does not show detectable differences in the precipitations in the diffusion zone – [Fig.3 a-b].

The process of Armco-Fe carbonitriding under the same conditions (Р 82% Ar +18% CO2 = 200Ра, [Table 4], [modes 5-6] leads to obtaining a layer with higher micro hardness (HV0.1= 4400 MPa) than in the process of nitriding - HV0.1= 4200 MPa. It can be seen from [Fig.2.2c] that in the obtained carbonitrided layer there are carbonitrided (nitrided) precipitations with smaller sizes but in greater amount than in the layer, obtained after treatment with a bigger amount of ammonia (90% NH3 + 8.2%Ar + 1.8 % CO2).

After 25GrMnSiNiMo steel carbonitriding under the mode 7 [Table 4] in a gas medium of 70% NH3 + 24.6%Ar + 5.4 % CO2 at the pressure of 400Ра, a 210 μm layer with maximum micro hardness HV0.1= 9300 МРа and combined zone thickness of 6 μm is obtained.

During the process of Armco-Fe carbonitriding under the same mode [mode 7], [Table 1] a layer with highest surface micro hardness of HV0.1= 4800 МРа is obtained, in comparison to all the modes of treatment, considered so far. In the diffusion zone of the formed carbonitrided layer carbonitrided (nitrided) precipitations are observed [Fig. 2.3], which are of smaller sizes and in greater amount than the ones, obtained at using 90% NH3 and 10 % corgon [Table 4,modes 2- 3,Fig.2.]; and bigger in size but in a smaller amount at carbonitriding with 50% NH3 and 50 % carbon [Table 1, modes 5-6, Fig.3]. This is probably due to the diffusion of carbon in the diffusion zone of the carbonitrided layer as well. Together with the increase of the pressure of the gas medium to 700Ра (NH3 - 350 Ра and corgon -350 Ра – [modes 9-10, Table 1] in the process of carbonitriding of the two materials under investigation, layers with essential differences are formed. After 25GrMnSiNiMo steel carbonitriding layers with a lowest surface micro hardness (HV0.1= 7400 - 7500 МРа) and total thickness (140 -230 μm) in comparison to all the other modes of nitriding and carbonitriding are obtained. The white zone is non-uniform and broken – [Fig.4]. This is probably due to the increased amount of argon in the gas medium and the high density of the current at the higher pressure of the gas medium, as well as to the low voltage of the discharge [380V, Table 4.].

120 Heat Treatment – Conventional and Novel Applications

**Figure 2.** Microstructure of 25GrMnSiNiMo steel [a] and Armco-Fe [b, c] after carbonitriding at: t =

detectable differences in the precipitations in the diffusion zone – [Fig.3 a-b].

Together with the increase in the pressure of carbon (Р 82% Ar +18% CO2 = 200Ра, [Table 4] in a gas medium, in case of 25GrMnSiNiMo steel treatment carbonitrided layers are formed, having lower micro hardness (HV0.1= 8900- 9200 МРа), total thickness (150-240 μm) and combined zone thickness (5-8 μm), than under the modes of treatment, considered so far. It is due to the increased activity of pulverizing, since the amount of argon in the gas medium is bigger - 41%. The higher rate of pulverizing leads to decreasing the probability for collisions between the atoms and ions, in consequence of which smaller amount of nitrogen and carbon is delivered to the surface. The microstructure analysis of the layer does not show

The process of Armco-Fe carbonitriding under the same conditions (Р 82% Ar +18% CO2 = 200Ра, [Table 4], [modes 5-6] leads to obtaining a layer with higher micro hardness (HV0.1= 4400 MPa) than in the process of nitriding - HV0.1= 4200 MPa. It can be seen from [Fig.2.2c] that in the obtained carbonitrided layer there are carbonitrided (nitrided) precipitations with smaller sizes but in greater amount than in the layer, obtained after treatment with a bigger

After 25GrMnSiNiMo steel carbonitriding under the mode 7 [Table 4] in a gas medium of 70% NH3 + 24.6%Ar + 5.4 % CO2 at the pressure of 400Ра, a 210 μm layer with maximum

During the process of Armco-Fe carbonitriding under the same mode [mode 7], [Table 1] a layer with highest surface micro hardness of HV0.1= 4800 МРа is obtained, in comparison to all the modes of treatment, considered so far. In the diffusion zone of the formed carbonitrided layer carbonitrided (nitrided) precipitations are observed [Fig. 2.3], which are of smaller sizes and in greater amount than the ones, obtained at using 90% NH3 and 10 % corgon [Table 4,modes 2- 3,Fig.2.]; and bigger in size but in a smaller amount at

micro hardness HV0.1= 9300 МРа and combined zone thickness of 6 μm is obtained.

550С, Р NH3 = 360Pa, Р 82% Ar +18% CO2 = 40Ра; а, c - τ = 6h, b - τ = 2 h

amount of ammonia (90% NH3 + 8.2%Ar + 1.8 % CO2).

**Figure 3.** Microstructure of 25GrMnSiNiMo steel [а, b] and Armco-Fe[c] after carbonitriding at: t = 550С, Р NH3 = 200Pa, Р 82% Ar +18% CO2 = 200Ра; а, c - τ = 2h, b - τ = 6h

After Armco-Fe carbonitriding under the same modes of treatment a layer with highest micro hardness (HV0.1= 5400-5600 МРа) and lowest combined zone thickness (4 μm) in comparison to all the other modes of nitriding and carboniding is obtained. In the diffusion zone of the carbonitrided layer the smallest amount of precipitations with the smallest sizes in comparison to all the other modes of carbonitriding is observed.

Under the same mode of treatment, 25GrMnSiNiMo steel possesses higher micro hardness and smaller total thickness of the nitrided and carbonitrided layer, than Armco-Fe. After certain treatment of 25GrMnSiNiMo steel with an additionally introduced carboncontaining gas (carbon) in the ammonia medium at different percentage ratios layers with lower depth, surface hardness and combined zone thickness than in the process of nitriding are obtained.

After conducting the process of carbonitriding of the investigated materials with carbon (82 % Ar + 18 % CO2) and ammonia, layers of small combined zone thickness are obtained. For

#### 122 Heat Treatment – Conventional and Novel Applications

Armco-Fe the thickness is within 4 to 8 μm. During the process of nitriding of technical iron, a nitrided layer is formed, having the biggest combined zone [10 μm, mode 4, Table 4], which is not valid for the other modes of nitriding. The increase in the duration of the process and the decrease in carbon pressure lead to combined zone growth. During the process of 25GrMnSiNiMo steel carbonitriding this dependence remains the same. After 25GrMnSiNiMo steel nitriding a layer with a bigger combined zone is observed, than during the process of carbonitriding (6-11 μm against 4-8 μm). This is explained by the stronger pulverizing action of plasma as a consequence of the increase in current density and decrease in voltage after introducing carbon into the ammonia medium.

Carbonitriding of Materials in Low Temperature Plasma 123

N-Concentration [mass %]

0

5

10

15

= -

= 584

It can be seen [Table 5] that after ion carbonitriding of Armco-iron at tnitr. = 823K (550°С), РNH3 = 280Pa, τ = 4h, a carbonitrided layer with total thickness δtot=280μm, compound zone thickness δсz = 6,5 μm and maximum micro-hardness of 480HV0.1 is obtained. In the so formed layer compressive residual stresses occur. From the three methods of defining the diffraction angles the method of maximum intensity is the one from which the highest value

carbonitriding in the surface layer of Armco-Fe are much lower than those of 25CrMnSiNiMo. During the process of Armco-Fe carbonitriding, a diffusion layer with bigger specific volume is formed, than it occurs with alloyed steel. This can be explained by the bigger total amount of nitrogen and carbon in depth the carbonitrided layer for

**Figure 4.** Nitrogen and carbon profile analysis according to GDOES in depth of a layer, carbonitrided

Depth [µm]

<sup>0</sup> <sup>5</sup> <sup>10</sup> <sup>15</sup> 0,0

C

N

Because of the lack of alloying elements in the Armco-Fe, no special carbonitrides are formed in it, and the difference in the specific volumes of the carbonitrided layer and the core material is therefore smaller. This leads to reducing the value of the residual stresses

After ion carbonitriding of 25CrMnSiNiMo steel at tnitr. = 823K (550°С), Р1NH3 = 200Pa, Р2carbon = 200Pa, τ = 2h, a carbonitrided layer with total thickness δtot =150μm, compound zone thickness δсz = 4.5μm and maximum micro-hardness of 890HV0.1 is obtained. In thus obtained carbonitrided layer residual compressive stresses with the highest value of σφ<sup>s</sup>

With prolongation of the time of 25CrMnSiNiMo-steel carbonitriding from 2 to 4 hours and reducing the carbon pressure from 200 to 120 Pa while increasing ammonia pressure from 200 to 280 Pa, a carbonitrided layer with higher total thickness δtot = 210μm, compound zone thickness δсz = 6.3 μm, and higher maximum micro-hardness - 930HV0.1 - is formed. The resultant compressive stresses on the carbonitrided surface are lowered to σφ<sup>s</sup>

at: t = 823K (550oC), P1 ammonia =280Ра, P carbon =120Ра, τ = 4h, 25CrMnSiNiMo

formed in the carbonitrided layer in Armco-Fe.

0,5

1,0

C-Concentration [mass %]

1,5

829 MPa are formed.

= - 54MРa) results. The compressive stresses, resulting after the ion

of residual stresses (σφ<sup>s</sup>

25CrMnSiNiMo steel [Fig.4].

It could be noted that the use of carbon together with ammonia in the process of carbonitriding leads to decrease in the pressure of plasma discharge, which depends on the ratio between the two gases. When introducing carbon into the camera, the pressure of the discharge falls down. In order to reach the required temperature of carbonitriding in this case it is necessary to increase the current of the discharge. Thus the power of plasma remains the same. The increase of the current density leads to an increase in the pulverizing action of plasma, despite of the low voltage level. This is explained by the bigger amount of ions, bombing the surface of the detail. The bigger current density does not lead to an increase in the kinetic energy of the ions. The decrease in the pressure of the gases in the camera causes an increase in the discharge voltage and the kinetic energy of the ions increases at the same time as a result, though their amount remains unchanged. The coefficient of pulverizing could also be increased this way, which would lead to a decrease in the combined zone thickness.

## **3.2. Roentgenographic determination of internal stresses**

By means of the Roentgen diffraction-meter the diffraction angles at different angles of rotation of the sample - Ψ и φ – are measured in the carbonitrided layers. The data are introduced into the program "MATHLAB-2008", by means of which graphs are built and the values of the angle 2θ for sin2Ψ, at Ψ=90**°** are calculated.

After defining the angle 2θ<sup>s</sup> at Ψ= 900 for all carbonitrided samples, residual compressive stresses in the carbonitrided layers have been calculated. The results are given in Table 5. Three ways of defining the diffraction angles have been used: the maximum intensity method - σφ<sup>s</sup> , the chord method - σφ<sup>c</sup> , and the body centre method - σφb.


**Table 5.** Results from the obtained residual stresses

It can be seen [Table 5] that after ion carbonitriding of Armco-iron at tnitr. = 823K (550°С), РNH3 = 280Pa, τ = 4h, a carbonitrided layer with total thickness δtot=280μm, compound zone thickness δсz = 6,5 μm and maximum micro-hardness of 480HV0.1 is obtained. In the so formed layer compressive residual stresses occur. From the three methods of defining the diffraction angles the method of maximum intensity is the one from which the highest value of residual stresses (σφ<sup>s</sup> = - 54MРa) results. The compressive stresses, resulting after the ion carbonitriding in the surface layer of Armco-Fe are much lower than those of 25CrMnSiNiMo. During the process of Armco-Fe carbonitriding, a diffusion layer with bigger specific volume is formed, than it occurs with alloyed steel. This can be explained by the bigger total amount of nitrogen and carbon in depth the carbonitrided layer for 25CrMnSiNiMo steel [Fig.4].

122 Heat Treatment – Conventional and Novel Applications

in the combined zone thickness.

After defining the angle 2θ<sup>s</sup>

method - σφ<sup>s</sup>

Material

Armco-Fe the thickness is within 4 to 8 μm. During the process of nitriding of technical iron, a nitrided layer is formed, having the biggest combined zone [10 μm, mode 4, Table 4], which is not valid for the other modes of nitriding. The increase in the duration of the process and the decrease in carbon pressure lead to combined zone growth. During the process of 25GrMnSiNiMo steel carbonitriding this dependence remains the same. After 25GrMnSiNiMo steel nitriding a layer with a bigger combined zone is observed, than during the process of carbonitriding (6-11 μm against 4-8 μm). This is explained by the stronger pulverizing action of plasma as a consequence of the increase in current density and

It could be noted that the use of carbon together with ammonia in the process of carbonitriding leads to decrease in the pressure of plasma discharge, which depends on the ratio between the two gases. When introducing carbon into the camera, the pressure of the discharge falls down. In order to reach the required temperature of carbonitriding in this case it is necessary to increase the current of the discharge. Thus the power of plasma remains the same. The increase of the current density leads to an increase in the pulverizing action of plasma, despite of the low voltage level. This is explained by the bigger amount of ions, bombing the surface of the detail. The bigger current density does not lead to an increase in the kinetic energy of the ions. The decrease in the pressure of the gases in the camera causes an increase in the discharge voltage and the kinetic energy of the ions increases at the same time as a result, though their amount remains unchanged. The coefficient of pulverizing could also be increased this way, which would lead to a decrease

By means of the Roentgen diffraction-meter the diffraction angles at different angles of rotation of the sample - Ψ и φ – are measured in the carbonitrided layers. The data are introduced into the program "MATHLAB-2008", by means of which graphs are built and

stresses in the carbonitrided layers have been calculated. The results are given in Table 5. Three ways of defining the diffraction angles have been used: the maximum intensity

HV0.1

Аrmcо-Fe 4 280 120 480 280 6.5 -54 -28 -14 25CrMnSiNiMo 4 280 120 930 210 6.3 -584 -621 -521 25CrMnSiNMo 2 200 200 890 150 4.5 -829 -713 -655 25CrMnSiNiMo 2 350 350 740 140 4.1 -90 -63 -41

, and the body centre method - σφb.

δtot

[μm]

at Ψ= 900 for all carbonitrided samples, residual compressive

δс<sup>z</sup>

σφ<sup>s</sup>

σφ<sup>c</sup>

σφ<sup>b</sup>

[MPa]

[MPa]

[MPa]

[μm]

decrease in voltage after introducing carbon into the ammonia medium.

**3.2. Roentgenographic determination of internal stresses** 

the values of the angle 2θ for sin2Ψ, at Ψ=90**°** are calculated.

P1 NH3 [Pa]

P2 corgon [Pa]

, the chord method - σφ<sup>c</sup>

τ

[h]

**Table 5.** Results from the obtained residual stresses

**Figure 4.** Nitrogen and carbon profile analysis according to GDOES in depth of a layer, carbonitrided at: t = 823K (550oC), P1 ammonia =280Ра, P carbon =120Ра, τ = 4h, 25CrMnSiNiMo

Because of the lack of alloying elements in the Armco-Fe, no special carbonitrides are formed in it, and the difference in the specific volumes of the carbonitrided layer and the core material is therefore smaller. This leads to reducing the value of the residual stresses formed in the carbonitrided layer in Armco-Fe.

After ion carbonitriding of 25CrMnSiNiMo steel at tnitr. = 823K (550°С), Р1NH3 = 200Pa, Р2carbon = 200Pa, τ = 2h, a carbonitrided layer with total thickness δtot =150μm, compound zone thickness δсz = 4.5μm and maximum micro-hardness of 890HV0.1 is obtained. In thus obtained carbonitrided layer residual compressive stresses with the highest value of σφ<sup>s</sup> = - 829 MPa are formed.

With prolongation of the time of 25CrMnSiNiMo-steel carbonitriding from 2 to 4 hours and reducing the carbon pressure from 200 to 120 Pa while increasing ammonia pressure from 200 to 280 Pa, a carbonitrided layer with higher total thickness δtot = 210μm, compound zone thickness δсz = 6.3 μm, and higher maximum micro-hardness - 930HV0.1 - is formed. The resultant compressive stresses on the carbonitrided surface are lowered to σφ<sup>s</sup> = 584 MPa. The explanation can be found in the phase composition and the thickness of the compound zone (δсz=6.3 μm).

Carbonitriding of Materials in Low Temperature Plasma 125

0

5

10

N-Concentration [mass %]

15

Depending on the concentration of nitrogen and carbon in the carbonitrided layer, as well as on the alloying elements contained in the materials, the specific volume of the surface changes; this, in turn, leads to forming residual compressive stresses of different values.

**3.3. Results from the analysis and the investigations of 25CrMnSiNiMo steel** 

10μm. The distribution of the diffused in depth nitrogen is given in [Fig. 6].

C

N

After nitriding under the mode 6 [Table 2] a layer is formed in 25CrMnSiNiMo steel with micro-hardness of 1072HV0,1, total thickness of 250 μm and combined zone thickness of

**Figure 6.** Carbon (С) and nitrogen (N) concentration in depth after carbonitriding of 25CrMnSiNiMo

<sup>0</sup> <sup>5</sup> <sup>10</sup> <sup>15</sup> 0,0

Depth [µm]

When, except for ammonia, 10% corgon is introduced into the chamber in addition, a carbonitrided layer with lower total thickness (290 μm) and combined zone thickness (8μm)

It can be noted that after carbonitriding in the media of 90% NH3 + 8.2% Ar + 1.8 % CO2 at 400Ра pressure, a layer with lower micro-hardness, total thickness and combined zone thickness, than after the process of nitriding, is obtained. This is probably due to the availability of carbon in the saturating medium, which, owing to its bigger atomic mass, has strong pulverizing action. With the high coefficient of pulverization the length of the free run of the pulverized atoms is bigger and the possibility for backward diffusion of the nitrogen and carbon is lower. Lower concentration of nitrogen (10%) and higher content of carbon by nearly 50% is obtained in the combined zone of the carbonitrided layer, compared

It can be seen from [Fig.6] that the concentration of carbon (0.48%) has increased at the border between the basic material and the combined zone, while under the carbonitride zone gradual change of the carbon content has been observed. This can be explained by the simultaneous saturation of the surface both with nitrogen and carbon, where part of the

steel at: t = 550 0C, P NH3 = 360 Pa, P 82% Ar + 18% CO2 = 40 Pa, τ = 6 h

than they are in the nitrided layer is obtained.

0,5

C-Concentration [mass %]

1,0

1,5

nitrogen atoms is replaced by the carbon ones.

to the nitrided one – [Fig.6].

Together with increasing ammonia and carbon pressure from 200 to 350Pa for 2 hours' time of treatment a carbonitrided layer with total thickness δtot =140μm, compound zone thickness δсz = 4.1μm and maximum micro-hardness 740HV0.1 is obtained. In the carbonitrided layer, obtained this way, the smallest residual compressive stresses of σφ<sup>s</sup> = - 90MPa are formed. The high pressure of the two saturating gases Рtot = 700 Pa does not activate the process of pulverizing and therefore a bigger amount of nitrogen and carbon is delivered to the surface. This probably leads to forming a bigger amount of micro-pores in the white zone [Fig.5], as a consequence of which the specific volume of the carbonitrided surface formed is bigger than the one in the core material.

**Figure 5.** Microstructure of 25CrMnSiNiMo -steel after carbonitriding at: t = 823K (550С), РNH3=350Pa, Р 82% Ar +18% CO2 = 350Ра, τ = 2h

In the process of 25CrMnSiNiMo-steel ion carbonitriding the increase of ammonia pressure (P1MН3 = 200-350 Pa) in the saturating medium forms a carbonitrided layer with approximately the same total thickness (δtot = 140-150μm) and compound zone thickness (δсz= 4.1 – 4.5μm), but with lower micro-hardness (890 – 740 HV0,1). This leads to a considerable decrease of the residual compressive stresses on the carbonitrided surface (σφ<sup>s</sup> = 829 –90MPa).

It can be noted that under the same modes of ion carbonitriding [modes 1 and 2, Table 5] the two materials under investigation form different residual compressive stresses on their surfaces (σφ<sup>s</sup> = 54–584 MPa). This significant difference is explained by the availability of alloying elements in the 25CrMnSiNiMo-steel, which, after the process of carbonitriding, form disperse carbonitrides. This leads to certain increase in the micro-hardness and in the specific volume of the carbonitrided layer and thence, to increase in the residual compressive stresses on the surface as well.

It can be noted from the conducted investigations that the chosen modes of ion carbonitriding form on the surface of the materials carbonitride layers with a bigger specific volume than on the core.

Depending on the concentration of nitrogen and carbon in the carbonitrided layer, as well as on the alloying elements contained in the materials, the specific volume of the surface changes; this, in turn, leads to forming residual compressive stresses of different values.

## **3.3. Results from the analysis and the investigations of 25CrMnSiNiMo steel**

124 Heat Treatment – Conventional and Novel Applications

surface formed is bigger than the one in the core material.

compound zone (δсz=6.3 μm).

Р 82% Ar +18% CO2 = 350Ра, τ = 2h

compressive stresses on the surface as well.

= 829 –90MPa).

surfaces (σφ<sup>s</sup>

volume than on the core.

MPa. The explanation can be found in the phase composition and the thickness of the

Together with increasing ammonia and carbon pressure from 200 to 350Pa for 2 hours' time of treatment a carbonitrided layer with total thickness δtot =140μm, compound zone thickness δсz = 4.1μm and maximum micro-hardness 740HV0.1 is obtained. In the carbonitrided layer, obtained this way, the smallest residual compressive stresses of σφ<sup>s</sup>

90MPa are formed. The high pressure of the two saturating gases Рtot = 700 Pa does not activate the process of pulverizing and therefore a bigger amount of nitrogen and carbon is delivered to the surface. This probably leads to forming a bigger amount of micro-pores in the white zone [Fig.5], as a consequence of which the specific volume of the carbonitrided

**Figure 5.** Microstructure of 25CrMnSiNiMo -steel after carbonitriding at: t = 823K (550С), РNH3=350Pa,

In the process of 25CrMnSiNiMo-steel ion carbonitriding the increase of ammonia pressure (P1MН3 = 200-350 Pa) in the saturating medium forms a carbonitrided layer with approximately the same total thickness (δtot = 140-150μm) and compound zone thickness (δсz= 4.1 – 4.5μm), but with lower micro-hardness (890 – 740 HV0,1). This leads to a considerable decrease of the residual compressive stresses on the carbonitrided surface (σφ<sup>s</sup>

It can be noted that under the same modes of ion carbonitriding [modes 1 and 2, Table 5] the two materials under investigation form different residual compressive stresses on their

alloying elements in the 25CrMnSiNiMo-steel, which, after the process of carbonitriding, form disperse carbonitrides. This leads to certain increase in the micro-hardness and in the specific volume of the carbonitrided layer and thence, to increase in the residual

It can be noted from the conducted investigations that the chosen modes of ion carbonitriding form on the surface of the materials carbonitride layers with a bigger specific

= 54–584 MPa). This significant difference is explained by the availability of

= -

After nitriding under the mode 6 [Table 2] a layer is formed in 25CrMnSiNiMo steel with micro-hardness of 1072HV0,1, total thickness of 250 μm and combined zone thickness of 10μm. The distribution of the diffused in depth nitrogen is given in [Fig. 6].

**Figure 6.** Carbon (С) and nitrogen (N) concentration in depth after carbonitriding of 25CrMnSiNiMo steel at: t = 550 0C, P NH3 = 360 Pa, P 82% Ar + 18% CO2 = 40 Pa, τ = 6 h

When, except for ammonia, 10% corgon is introduced into the chamber in addition, a carbonitrided layer with lower total thickness (290 μm) and combined zone thickness (8μm) than they are in the nitrided layer is obtained.

It can be noted that after carbonitriding in the media of 90% NH3 + 8.2% Ar + 1.8 % CO2 at 400Ра pressure, a layer with lower micro-hardness, total thickness and combined zone thickness, than after the process of nitriding, is obtained. This is probably due to the availability of carbon in the saturating medium, which, owing to its bigger atomic mass, has strong pulverizing action. With the high coefficient of pulverization the length of the free run of the pulverized atoms is bigger and the possibility for backward diffusion of the nitrogen and carbon is lower. Lower concentration of nitrogen (10%) and higher content of carbon by nearly 50% is obtained in the combined zone of the carbonitrided layer, compared to the nitrided one – [Fig.6].

It can be seen from [Fig.6] that the concentration of carbon (0.48%) has increased at the border between the basic material and the combined zone, while under the carbonitride zone gradual change of the carbon content has been observed. This can be explained by the simultaneous saturation of the surface both with nitrogen and carbon, where part of the nitrogen atoms is replaced by the carbon ones.

#### 126 Heat Treatment – Conventional and Novel Applications

With the increase in the carbon pressure [P 82% Ar + 18% CO2 = 200 Pa, Table2, modes 3 and 4] in the gas medium, after carbonitriding of 25CrMnSiNiMo steel, carbonitrided layers are formed, having lower micro-hardness (890 – 920 HV0,1), total thickness (150 – 240 μm) and combined zone thickness than under the rest of the modes of treatment. This is due to the increased activity of pulverization, as the amount of argon in the gas medium is higher – 41%. The higher degree of pulverization leads to decreasing the probability for collisions between the atoms and ions, as a result of which lower amount of nitrogen and carbon is delivered to the surface. Lower concentration of nitrogen (20%) and increased content of carbon with nearly 20% is obtained in the combined zone of the carbonitrided layer in comparison with the nitrided one – [Fig.7].

Carbonitriding of Materials in Low Temperature Plasma 127

0

5

10

N-Concentration [mass %]

15

μm. The distribution of the nitrogen and carbon in depth of the carbonitrided zone changes

**Figure 8.** Distribution of carbon (С) and nitrogen (N)in depth after carbonitriding of 25CrMnSiNiMo

Depth [µm]

<sup>0</sup> <sup>5</sup> <sup>10</sup> <sup>15</sup> 0,0

C

N

Significant increase in the concentration of carbon at the beginning of the combined zone can be seen from [Fig. 8], where it reaches the level of 0.52% and slightly decreases at the end of the carbonitrided zone, going to about 0.48 %. The distribution of the nitrogen in the carbonitrided zone changes gradually and its concentration at the end of the combined zone reaches the level of 7%, while at the beginning of the combined zone it is about 12.2 %. Under this mode of treatment the highest level of nitrogen concentration 12.2 % is achieved in the combined zone and the most gradual change of the content of nitrogen and carbon in the formed layer occurs in comparison to all the other modes of ion carbonitriding of

In Armco-iron carbonitriding under the 4th mode of treatment (50%HN3 + 41% Ar + 9 %CO2) from Table 2 a layer with surface micro-hardness of 370HV0.1, total thickness of 210 μm and combined zone thickness of 6 μm is obtained and the distribution of nitrogen and carbon in

From [Fig.9] it can be seen that at the end of the combined zone at 6μm depth slight increase of the carbon content to 0.24 % is observed, while at the beginning of the combined zone the carbon content reaches 1 %. The figure shows that the distribution of carbon in depth of the combined zone is sharp to 3μm depth with concentration of 0.20 %. At the end of the carbonitrided zone the carbon concentration increases to 0.24 %. The nitrogen distribution change in the carbonitrided layer goes gradually. At the end of the combined zone (6μm) its

concentration reaches 3.4 %, while at its beginning the concentration is 8.3%.

gradually, staying almost the same up to 7.5 μm – [Fig.8].

steel at: t = 550 0C, P NH3 = 280 Pa, P 82% Ar + 18% CO2 = 120 Pa, τ = 4 h

0,5

C-Concentration [mass %]

1,0

1,5

depth of the carbonitrided zone is given in [Fig. 9].

25CrMnSiNiMo steel.

**3.4. Armco-iron** 

**Figure 7.** Distribution of carbon (C) and nitrogen (N) in depth after carbonitriding of 25CrMnSiNiMo steel at: a) t = 550 0C, P NH3 = 200 Pa, P 82% Ar + 18% CO2 = 200 Pa, τ = 2h, b) t = 550 0C: PNH3 = 200 Pa, P82% Ar + 18% CO2 = 200 Pa, τ = 6 h

It can be seen from [Fig.7.a].that at the end of the combined zone of the layer, at 5 μm depth, slight increase of the carbon up to 0.3 % is observed, while at the beginning of the combined zone the carbon is over 0.5 %. The concentration of the nitrogen in the carbonitrided zone decreases sharply, reaching at the end of the combined zone the level of 4.9 %, while the nitrogen on the surface is 9.1%.

With prolongation of the time of carbonitriding from 2 to 6h the micro-hardness and the combined zone thickness increase. Significant increase in the concentration of carbon in the combined zone can be seen from [Fig.8], where it achieves the level of 0.81% on the surface and slightly decreases at the end of the zone – down to about 0.5%. The distribution of the nitrogen in the carbonitrided zone decreases gradually. At the border between the diffusion zone and the combined zone the nitrogen concentration is 5.8 %, while on the surface it is 10.5%.

After carbonitriding of 25CrMnSiNiMo steel under the 5th mode of treatment [Table 2] in the gas medium of 70% NH3 + 24.6 % Ar + 5.4 % CO2 at 400 Ра pressure, a layer is obtained with total thickness 210 μm, maximum micro-hardness 930HV0.1 and combined zone thickness 9 μm. The distribution of the nitrogen and carbon in depth of the carbonitrided zone changes gradually, staying almost the same up to 7.5 μm – [Fig.8].

**Figure 8.** Distribution of carbon (С) and nitrogen (N)in depth after carbonitriding of 25CrMnSiNiMo steel at: t = 550 0C, P NH3 = 280 Pa, P 82% Ar + 18% CO2 = 120 Pa, τ = 4 h

Significant increase in the concentration of carbon at the beginning of the combined zone can be seen from [Fig. 8], where it reaches the level of 0.52% and slightly decreases at the end of the carbonitrided zone, going to about 0.48 %. The distribution of the nitrogen in the carbonitrided zone changes gradually and its concentration at the end of the combined zone reaches the level of 7%, while at the beginning of the combined zone it is about 12.2 %. Under this mode of treatment the highest level of nitrogen concentration 12.2 % is achieved in the combined zone and the most gradual change of the content of nitrogen and carbon in the formed layer occurs in comparison to all the other modes of ion carbonitriding of 25CrMnSiNiMo steel.

### **3.4. Armco-iron**

126 Heat Treatment – Conventional and Novel Applications

comparison with the nitrided one – [Fig.7].

<sup>0</sup> <sup>5</sup> <sup>10</sup> <sup>15</sup> 0,0

Depth [µm]

C

N

CO2 = 200 Pa, τ = 6 h

0,5

C-Concentration [mass %]

1,0

1,5

10.5%.

nitrogen on the surface is 9.1%.

With the increase in the carbon pressure [P 82% Ar + 18% CO2 = 200 Pa, Table2, modes 3 and 4] in the gas medium, after carbonitriding of 25CrMnSiNiMo steel, carbonitrided layers are formed, having lower micro-hardness (890 – 920 HV0,1), total thickness (150 – 240 μm) and combined zone thickness than under the rest of the modes of treatment. This is due to the increased activity of pulverization, as the amount of argon in the gas medium is higher – 41%. The higher degree of pulverization leads to decreasing the probability for collisions between the atoms and ions, as a result of which lower amount of nitrogen and carbon is delivered to the surface. Lower concentration of nitrogen (20%) and increased content of carbon with nearly 20% is obtained in the combined zone of the carbonitrided layer in

**Figure 7.** Distribution of carbon (C) and nitrogen (N) in depth after carbonitriding of 25CrMnSiNiMo steel at: a) t = 550 0C, P NH3 = 200 Pa, P 82% Ar + 18% CO2 = 200 Pa, τ = 2h, b) t = 550 0C: PNH3 = 200 Pa, P82% Ar + 18%

(a) (b)

<sup>0</sup> <sup>5</sup> <sup>10</sup> <sup>15</sup> 0,0

Depth [µm]

0

5

10

N-Concentration [mass %]

15

0

5

10

N-Concentration [mass %]

0,5

C-Concentration [mass %]

C

N

1,0

1,5

15

It can be seen from [Fig.7.a].that at the end of the combined zone of the layer, at 5 μm depth, slight increase of the carbon up to 0.3 % is observed, while at the beginning of the combined zone the carbon is over 0.5 %. The concentration of the nitrogen in the carbonitrided zone decreases sharply, reaching at the end of the combined zone the level of 4.9 %, while the

With prolongation of the time of carbonitriding from 2 to 6h the micro-hardness and the combined zone thickness increase. Significant increase in the concentration of carbon in the combined zone can be seen from [Fig.8], where it achieves the level of 0.81% on the surface and slightly decreases at the end of the zone – down to about 0.5%. The distribution of the nitrogen in the carbonitrided zone decreases gradually. At the border between the diffusion zone and the combined zone the nitrogen concentration is 5.8 %, while on the surface it is

After carbonitriding of 25CrMnSiNiMo steel under the 5th mode of treatment [Table 2] in the gas medium of 70% NH3 + 24.6 % Ar + 5.4 % CO2 at 400 Ра pressure, a layer is obtained with total thickness 210 μm, maximum micro-hardness 930HV0.1 and combined zone thickness 9 In Armco-iron carbonitriding under the 4th mode of treatment (50%HN3 + 41% Ar + 9 %CO2) from Table 2 a layer with surface micro-hardness of 370HV0.1, total thickness of 210 μm and combined zone thickness of 6 μm is obtained and the distribution of nitrogen and carbon in depth of the carbonitrided zone is given in [Fig. 9].

From [Fig.9] it can be seen that at the end of the combined zone at 6μm depth slight increase of the carbon content to 0.24 % is observed, while at the beginning of the combined zone the carbon content reaches 1 %. The figure shows that the distribution of carbon in depth of the combined zone is sharp to 3μm depth with concentration of 0.20 %. At the end of the carbonitrided zone the carbon concentration increases to 0.24 %. The nitrogen distribution change in the carbonitrided layer goes gradually. At the end of the combined zone (6μm) its concentration reaches 3.4 %, while at its beginning the concentration is 8.3%.

Carbonitriding of Materials in Low Temperature Plasma 129

Under this mode of treatment a layer with surface micro-hardness of 430HV0.1, total thickness of 260 μm and combined zone thickness of 6μm is obtained. The concentration of carbon in depth of the layer is relatively low and reaches 0.48 % on the surface, while at 4.3 μm from the surface it has the lowest value (0.16 %). At the end of the combined zone the concentration slightly increases (0.21 %). The distribution of nitrogen in the carbonitrided zone goes up gradually, reaching on the surface the level of 8.1 % and decreasing to 3.9 % at 4.3μm from the surface. Under this mode of carbonitriding the carbon and nitrogen concentration changes gradually; however, their concentration is lower in depth of the

It can be noted that when in the process of carbonitriding the saturating medium contains bigger amount of СО2 (9%), on the surface of Armco-iron combined zone with highest carbon concentration 1% is formed, while at (1.8 %) content of СО2 the concentration is the lowest - 0.48%. From the modes of carbonitriding of Armco-iron under consideration the most uniform distribution of nitrogen and carbon in depth of the layer is observed under the 5th mode [Table 2]. The active role of argon for delivering carbon and nitrogen on the surface of the treated material is worth mentioning. As a result of its bigger atomic mass, argon has strong pulverizing action. With the high coefficient of pulverization the length of the free run of the pulverized atoms is bigger and the possibility for backward diffusion of carbon and nitrogen is lower. By changes in the pressure, as well as in the content of argon in the saturating medium, the backward diffusion of nitrogen and carbon can be regulated, thus

On the basis of the conducted glow discharge optical emission spectral analysis of samples from Armco-iron and 25CrMnSiNiMo steel it is necessary to note that under all modes of ion carbonitriding carried out in ammonia and carbon medium layers are formed with concentration of carbon in the combined zone, which, for the 25CrMnSiNiMo steel is within

It is necessary to note that two areas could be distinguished in the structure of the glow discharge: the zone of the discharge, where the processes of dissociation of the employed gases (СО2, NH3, Аr) occur, and the zone of the discharge, where reactions of recombination proceed. Carbon dioxide dissociation has been investigated by a great number of authors both theoretically and experimentally by using various sources of plasma such as a microwave discharge, a plasma reactive burner or radio frequency arc discharge. Despite the numerous works the kinetic mechanism of СО<sup>2</sup> dissociation has not been studied very well yet [2.5]. Actually the mechanism of СО2 dissociation is determined mainly by the parameters of the glow discharge (average energy of the electrons in the plasma) and the properties of the

In the cathode space of the glow discharge [Fig.11] the ordered motion of electrons and the position of the positively charged ions is the predominant event, while in the anode section the chaotic motion of the electrically charged particles prevails. Electrons are detached from

combined zone than it is under the 5th mode of treatment [Table 2].

making it possible to obtain layers with different features and properties.

**3.5. Dissociation and ionization of carbon dioxide and ammonia** 

0.6 % - 1.4 %, while for Armco-iron it is between 0.45% and 1 %.

plasma gas (pressure, velocity of flow, energy) [10.11].

**Figure 9.** Distribution of carbon (С) and nitrogen (N)in Armco-iron after carbonitriding t = 550 0C, P NH3 = 200 Pa, P 82% Ar + 18% CO2 = 200 Pa, τ = 2

After ion carbonitriding of Armco-iron under the 5th mode (70%HN3 + 24.6% Ar + 5.4 %CO2), a layer with the highest surface micro-hardness 480HV0.1 is obtained, in comparison to all the other modes of treatment, which can be explained by the distribution of carbon and nitrogen in the carbonitrided zone – [Fig. 10a]. The figure illustrates that in depth of the combined zone increased carbon concentration of up to 0.68 % on the surface is observed, while it stays almost constant (0.65 %) at 3 μm depth. After that, at 6μm, sharp decrease of the carbon content is observed, together with its increase (0.25%) at the end of the carbonitride zone of the layer. The distribution of nitrogen in the carbonitride zone goes up gradually reaching 8.5 % on the surface, while at 3μm depth it is 5.1 %. It can be noted that under this mode of carbonitriding the nitrogen and carbon concentration changes more gradually and this concentration is higher in depth of the carbonitrided zone of the layer.

**Figure 10.** Distribution of carbon (С) and nitrogen (N) in Armco-iron, after carbonitriding at: а) t = 550 0C, P NH3 = 280 Pa, P 82% Ar + 18% CO2 = 120 Pa, τ = 4 h, b) t = 550 0C, P NH3 = 360 Pa, P 82% Ar + 18% CO2 = 40 Pa, τ = 2 h

[Fig.10.b] illustrates the distribution of carbon and nitrogen in Armco-iron after carbonitriding at: t = 550 0C, P NH3 = 360 Pa, τ = 2 h, P 82% Ar + 18% CO2= 40 Pa.

Under this mode of treatment a layer with surface micro-hardness of 430HV0.1, total thickness of 260 μm and combined zone thickness of 6μm is obtained. The concentration of carbon in depth of the layer is relatively low and reaches 0.48 % on the surface, while at 4.3 μm from the surface it has the lowest value (0.16 %). At the end of the combined zone the concentration slightly increases (0.21 %). The distribution of nitrogen in the carbonitrided zone goes up gradually, reaching on the surface the level of 8.1 % and decreasing to 3.9 % at 4.3μm from the surface. Under this mode of carbonitriding the carbon and nitrogen concentration changes gradually; however, their concentration is lower in depth of the combined zone than it is under the 5th mode of treatment [Table 2].

128 Heat Treatment – Conventional and Novel Applications

0,5

1,0

C-Concentration [mass %]

1,5

= 200 Pa, P 82% Ar + 18% CO2 = 200 Pa, τ = 2

**Figure 9.** Distribution of carbon (С) and nitrogen (N)in Armco-iron after carbonitriding t = 550 0C, P NH3

<sup>0</sup> <sup>5</sup> <sup>10</sup> <sup>15</sup> 0,0

Depth [µm]

C

N

N-Concentration [mass %]

0

<sup>0</sup> <sup>5</sup> <sup>10</sup> <sup>15</sup> 0,0

Depth [µm]

N-Concentration [mass %]

0

5

10

15

C

N

5

10

15

After ion carbonitriding of Armco-iron under the 5th mode (70%HN3 + 24.6% Ar + 5.4 %CO2), a layer with the highest surface micro-hardness 480HV0.1 is obtained, in comparison to all the other modes of treatment, which can be explained by the distribution of carbon and nitrogen in the carbonitrided zone – [Fig. 10a]. The figure illustrates that in depth of the combined zone increased carbon concentration of up to 0.68 % on the surface is observed, while it stays almost constant (0.65 %) at 3 μm depth. After that, at 6μm, sharp decrease of the carbon content is observed, together with its increase (0.25%) at the end of the carbonitride zone of the layer. The distribution of nitrogen in the carbonitride zone goes up gradually reaching 8.5 % on the surface, while at 3μm depth it is 5.1 %. It can be noted that under this mode of carbonitriding the nitrogen and carbon concentration changes more gradually and this concentration is higher in depth of the carbonitrided zone of the layer.

**Figure 10.** Distribution of carbon (С) and nitrogen (N) in Armco-iron, after carbonitriding at: а) t = 550 0C, P NH3 = 280 Pa, P 82% Ar + 18% CO2 = 120 Pa, τ = 4 h, b) t = 550 0C, P NH3 = 360 Pa, P 82% Ar + 18% CO2 = 40 Pa, τ = 2 h

(a) (b)

N-Concentration [mass %]

0,5

1,0

C-Concentration [mass %]

1,5

0

5

10

15

[Fig.10.b] illustrates the distribution of carbon and nitrogen in Armco-iron after

carbonitriding at: t = 550 0C, P NH3 = 360 Pa, τ = 2 h, P 82% Ar + 18% CO2= 40 Pa.

<sup>0</sup> <sup>5</sup> <sup>10</sup> <sup>15</sup> 0,0

Depth [µm]

C N

0,5

1,0

C-Concentration [mass %]

1,5

It can be noted that when in the process of carbonitriding the saturating medium contains bigger amount of СО2 (9%), on the surface of Armco-iron combined zone with highest carbon concentration 1% is formed, while at (1.8 %) content of СО2 the concentration is the lowest - 0.48%. From the modes of carbonitriding of Armco-iron under consideration the most uniform distribution of nitrogen and carbon in depth of the layer is observed under the 5th mode [Table 2]. The active role of argon for delivering carbon and nitrogen on the surface of the treated material is worth mentioning. As a result of its bigger atomic mass, argon has strong pulverizing action. With the high coefficient of pulverization the length of the free run of the pulverized atoms is bigger and the possibility for backward diffusion of carbon and nitrogen is lower. By changes in the pressure, as well as in the content of argon in the saturating medium, the backward diffusion of nitrogen and carbon can be regulated, thus making it possible to obtain layers with different features and properties.

On the basis of the conducted glow discharge optical emission spectral analysis of samples from Armco-iron and 25CrMnSiNiMo steel it is necessary to note that under all modes of ion carbonitriding carried out in ammonia and carbon medium layers are formed with concentration of carbon in the combined zone, which, for the 25CrMnSiNiMo steel is within 0.6 % - 1.4 %, while for Armco-iron it is between 0.45% and 1 %.

## **3.5. Dissociation and ionization of carbon dioxide and ammonia**

It is necessary to note that two areas could be distinguished in the structure of the glow discharge: the zone of the discharge, where the processes of dissociation of the employed gases (СО2, NH3, Аr) occur, and the zone of the discharge, where reactions of recombination proceed.

Carbon dioxide dissociation has been investigated by a great number of authors both theoretically and experimentally by using various sources of plasma such as a microwave discharge, a plasma reactive burner or radio frequency arc discharge. Despite the numerous works the kinetic mechanism of СО<sup>2</sup> dissociation has not been studied very well yet [2.5]. Actually the mechanism of СО2 dissociation is determined mainly by the parameters of the glow discharge (average energy of the electrons in the plasma) and the properties of the plasma gas (pressure, velocity of flow, energy) [10.11].

In the cathode space of the glow discharge [Fig.11] the ordered motion of electrons and the position of the positively charged ions is the predominant event, while in the anode section the chaotic motion of the electrically charged particles prevails. Electrons are detached from

#### 130 Heat Treatment – Conventional and Novel Applications

the cathode and they are accelerated in the direction towards the anode, acquiring energy, sufficient for dissociation and ionization of the atoms and molecules. The obtained positive ions are directed toward the cathode (C) and, colliding with its surface, they cause an emission of new electrons, while the secondary electrons, formed during the ionization, are accelerated by the field toward the anode (A).The cathode dark space in the structure of the glow discharge [Fig.11] includes the whole area of the cathode up to the next section of the negative glowing. This area is related to a big part of the voltage, called cathode fall of the potential. In this area the gas glowing is weak, as the energy of the electrons is higher than the maximum for excitation. This energy is sufficient for causing dissociation and ionization of the employed gases. The electrons, originated from the ionization of the atoms, are accelerated by the field and move toward the area of the negative glowing.

Carbonitriding of Materials in Low Temperature Plasma 131

Dark anode space

(7)

СО2 + е- → СО2+ + е- + е- (energy of ionization – 13.8 eV)` (6)

For the initial process of ionization many different types of positive ions are obtained (СО+, 0+, 02+), but the most important is СО2+ , the others are usually neglected [11,12]. Recently the

Potential

Positive glowing

Cathode column Anode glow

**Cathode Anode** 

2 2 2 2

+− −

It can be noted that СО2+ molecules can be formed in two excited states and forming a stable СО2+ dominates. СО<sup>2</sup> dissociation is mainly due to vibration excitation caused by electron collisions. It is clear in this case that by heating the employed gases in imbalanced conditions higher efficiency of dissociation can be achieved, since then the introduced energy is not used in all degrees of freedom. As the molecular dissociation goes due to vibration excitation, the effective dissociation could occur at imbalanced conditions, in which the increase in the vibration excited states is higher than it is at balanced conditions. Therefore it is assumed that molecular dissociation occurs in imbalanced plasma with high vibration temperature. With the imbalanced gas the efficiency of the dissociation increases for two reasons. The first reason is the comparatively smaller energy, used for excitation of translational and rotational degrees of freedom. The second reason is the inharmoniousness of the molecules, leading to an increase of the relative number of vibration excited molecules. Due to it the same extent of dissociation of the molecules is obtained at lower temperature of vibration, than the temperature at the lack of inharmoniousness. It can be noted that in the zone of the negative glowing of the glow discharge both processes of dissociation and ammonia ionization occur, leading to obtaining nitrogen and hydrogen by

СО е СО , СО е СО , СО е СО О

+ → + →+ +→ +

+ − + −

2

Negative glowing

Dark cathode space Faraday dark space

glow

**Figure 11.** Glow discharge structure

Aston dark space

c. ionization at electron collision

the following probable reactions:

following reactions have been identified [1,5]:

The gases in this area are in ionized state (plasma). The plasma results from the accelerated electrons, coming from the cathode dark space. At the moment the accelerated electrons impact the СО2 molecule, it decomposes in result from the bond breakage, which leads to forming СО, С and O, expressed by the following reactions [12, 13]:

a. Dissociation at direct electron impact:

$$\text{CO} + \text{e} \rightarrow \text{CO} + \text{e} \rightarrow \text{CO} + \text{O} - \text{532 kJ/mol (energy of dissociation - 7.3 eV)}\tag{1}$$

$$\text{CO} \leftrightarrow \text{C} + \text{O} - 1076 \text{ kJ/mol (energy of dissociation - 11.1 eV)}\tag{2}$$

$$\text{CO} \leftrightarrow \text{CO} + 1/2\text{O} - 281 \text{ kJ/mol (energy of dissociation} - 2.9 \text{ eV)}\tag{3}$$

$$\text{@:} \leftrightarrow \text{2O} - 497 \text{ kJ/mol (energy of dissociation} - 5.12 \text{ eV)} \tag{4}$$

The symbol \* corresponds to the state of high excitation. The addition of inert gases (Не, Ar ) into the CO2, medium leads to increasing the average energy of the electron in the discharge. At sufficient concentration of CO2, considerable reduction in the energy used for dissociation of one molecule is achieved.

It can be noted that with the increase in the vibration temperature the energy consumption for forming an atom reduces significantly since in these cases the decomposition of molecules is facilitated. However, the energy consumption for forming a carbon atom many times exceeds the energy for molecular dissociation. This is the case with СО. It can be explained first of all by the higher energy of dissociation of СО so that it considerably exceeds the average energy of the electron and the process of dissociation becomes a multiple-stage one.

b. dissociation bonding

$$\begin{aligned} \text{CO}\_2 + \text{e}^- &\rightarrow \text{(CO}\_2^-)^\* \rightarrow \text{CO} + \text{O} \\ &\rightarrow \text{C}^- + 2\text{O} \\ &\rightarrow \text{CO}^- + \text{O} \end{aligned} \tag{5}$$

During the reaction the negative ions from СО2 are minority [12]. The last reaction could lead to forming vibration excited СО2 molecules by recombination of СО and О, causing dissociation in СО + О after that.

**Figure 11.** Glow discharge structure

130 Heat Treatment – Conventional and Novel Applications

a. Dissociation at direct electron impact:

→ СО2\*

dissociation of one molecule is achieved.

+ e-

СО2+ e-

b. dissociation bonding

dissociation in СО + О after that.

the cathode and they are accelerated in the direction towards the anode, acquiring energy, sufficient for dissociation and ionization of the atoms and molecules. The obtained positive ions are directed toward the cathode (C) and, colliding with its surface, they cause an emission of new electrons, while the secondary electrons, formed during the ionization, are accelerated by the field toward the anode (A).The cathode dark space in the structure of the glow discharge [Fig.11] includes the whole area of the cathode up to the next section of the negative glowing. This area is related to a big part of the voltage, called cathode fall of the potential. In this area the gas glowing is weak, as the energy of the electrons is higher than the maximum for excitation. This energy is sufficient for causing dissociation and ionization of the employed gases. The electrons, originated from the ionization of the atoms, are

The gases in this area are in ionized state (plasma). The plasma results from the accelerated electrons, coming from the cathode dark space. At the moment the accelerated electrons impact the СО2 molecule, it decomposes in result from the bond breakage, which leads to

CO2 ↔CO + 1/2O2 – 281 kJ/ mol (energy of dissociation – 2.9 eV) (3)

The symbol \* corresponds to the state of high excitation. The addition of inert gases (Не, Ar ) into the CO2, medium leads to increasing the average energy of the electron in the discharge. At sufficient concentration of CO2, considerable reduction in the energy used for

It can be noted that with the increase in the vibration temperature the energy consumption for forming an atom reduces significantly since in these cases the decomposition of molecules is facilitated. However, the energy consumption for forming a carbon atom many times exceeds the energy for molecular dissociation. This is the case with СО. It can be explained first of all by the higher energy of dissociation of СО so that it considerably exceeds the average energy

\* СО2 2 <sup>е</sup> (СО ) СО О

+→ → +

During the reaction the negative ions from СО2 are minority [12]. The last reaction could

− −

of the electron and the process of dissociation becomes a multiple-stage one.

lead to forming vibration excited СО2 molecules by recombination of СО-

→ CO + O – 532 kJ/ mol (energy of dissociation - 7.3 eV) (1)

СО↔ С + О – 1076 kJ/ mol (energy of dissociation - 11.1 eV) (2)

О2 ↔ 2О – 497 kJ/ mol (energy of dissociation – 5.12 eV) (4)

С 2О СО О (5)

and О, causing

− −

→ + → +

accelerated by the field and move toward the area of the negative glowing.

forming СО, С and O, expressed by the following reactions [12, 13]:

c. ionization at electron collision

$$\text{COr + e^{-}} \rightarrow \text{COr + e^{-}} + \text{e} \quad \text{(energy of ionization} - 13.8 \,\text{eV}\text{)}\tag{6}$$

For the initial process of ionization many different types of positive ions are obtained (СО+, 0+, 02+), but the most important is СО2+ , the others are usually neglected [11,12]. Recently the following reactions have been identified [1,5]:

$$\begin{aligned} \text{CO}\_2^+ + \text{e}^- &\rightarrow \text{CO}\_2, \\ \text{CO}\_2^+ + \text{e}^- &\rightarrow \text{C} + \text{O}\_{2'} \\ \text{CO}\_2^+ + \text{e}^- &\rightarrow \text{CO}^- + \text{O} \end{aligned} \tag{7}$$

It can be noted that СО2+ molecules can be formed in two excited states and forming a stable СО2+ dominates. СО<sup>2</sup> dissociation is mainly due to vibration excitation caused by electron collisions. It is clear in this case that by heating the employed gases in imbalanced conditions higher efficiency of dissociation can be achieved, since then the introduced energy is not used in all degrees of freedom. As the molecular dissociation goes due to vibration excitation, the effective dissociation could occur at imbalanced conditions, in which the increase in the vibration excited states is higher than it is at balanced conditions. Therefore it is assumed that molecular dissociation occurs in imbalanced plasma with high vibration temperature. With the imbalanced gas the efficiency of the dissociation increases for two reasons. The first reason is the comparatively smaller energy, used for excitation of translational and rotational degrees of freedom. The second reason is the inharmoniousness of the molecules, leading to an increase of the relative number of vibration excited molecules. Due to it the same extent of dissociation of the molecules is obtained at lower temperature of vibration, than the temperature at the lack of inharmoniousness. It can be noted that in the zone of the negative glowing of the glow discharge both processes of dissociation and ammonia ionization occur, leading to obtaining nitrogen and hydrogen by the following probable reactions:

$$\text{NH:} \rightarrow \text{HNs}^{+} + \text{e}^{\cdot} \quad -164.65 \text{kJ/mol (energy of ionization - 1.69 eV)} \tag{8}$$

Carbonitriding of Materials in Low Temperature Plasma 133

the carbon (reaction СО2 + е- → СО2+ → С+ + 2О) and nitrogen (reaction NH3+ = N+ + 3H) atoms occur; these atoms impact the surface and diffuse at a certain distance into the material – [Fig.12]. The process of saturation of the metal surface depends only on the concentration of the atomic carbon and nitrogen in the plasma, as well as on the temperature of the article, while the electron or ion impact plays role for ensuring the

The availability of argon in the saturating medium in combination with CO2, leads to increasing the average energy in the discharge, which, at sufficient concentration of CO2, results in considerable reduction of the energy spent on the dissociation of a molecule.

In the process of carbonitriding part of the nitrogen atoms are replaced by the bigger carbon atoms, which causes forming the ε-phase in the carbonitrided layer. It is possible for two reasons: approximately the same ion radius of the nitrogen [rion = 13(5+1) pm, rion = 16(3+1) pm] and the carbon [rion = 16(4+1) pm]; the possibility for the carbon atoms to take up the vacant

1. It is established that, after ion carbonitriding of 25GrMnSiNiMo steel at the same temperature of treatment and time of saturation but different composition of the two gases in the vacuum camera (ammonia – 50, 70, 90, 100% and corgon - 50, 30 , 10%), the layers obtained have smaller thickness and micro hardness than after ion nitriding. 2. It is established that, the gases corgon and ammonia can be used in different percentage ratio in the role of saturating medium during the process of carbonitriding in glow

3. It has been established that the glow discharge optical emission spectroscopy can be used for investigating carbonitrided layers formed in low-temperature plasma in

4. It has been proved that after carbonitriding of the investigated materials at t=550 0C, PNH3 = 280 Pa, P 82% Ar + 18% CO2 = 120 Pa, τ = 4 h the most gradual change of the carbon and

5. Increased amount of carbon has been found both in the combined and in the diffusion

6. After carbonitriding in low temperature plasma, difference between the values of the residual compressive stresses, obtained by the three ways of defining diffraction angles

7. It has been established that, after the process of ion carbonitriding, the residual compressive stresses formed on the surface of the alloyed steel 25CrMnSiNiMo have a

8. It has been proved that in the process of ion carbonitriding of the investigated materials, the increase in the ammonia and carbon pressure in the vacuum chamber leads to a

9. A probable mechanism of glow discharge carbonintriding in a medium of ammonia, carbon dioxide and argon is suggested. As a consequence of the dissociation and

considerably higher value, than the value of these stresses in Armco-Fe.

decrease in the value of the residual compressive stresses.

, the cord method - σφ<sup>c</sup>

, and the method of the

nitrogen content in the carbonitrided zone of the layer occurs.

necessary temperature of the details.

junctions.

**4. Conclusion** 

discharge plasma.

ammonia and corgon medium.

zone of the carbonitrided layer.

(the method of maximum intensity - σφ<sup>s</sup>

body centre - σφb) has been established.

 NH3+ → N + + 3H – 2298.29kJ/mol (energy of ionization and dissociation-23.67 eV) (9) NH3+ = N + 2H +Н+ – 2216.96 kJ/mol (energy of ionization and dissociation - 22.83 eV) (10) NH3 = NH2 + H+ + e- – 1656.08 kJ/mol (energy of ionization and dissociation - 17.05eV) (11) NH2 = NH + H+ + e- – 1582.16 kJ/ mol (energy of ionization and dissociation – 16.29 eV) (12) NH = NH+ + e- – 1242.47 kJ/ mol (energy of ionization and dissociation – 12.79eV) (13) NH+ = N + H+ – 334.67 kJ/ mol (energy of ionization and dissociation – 3.44 eV) (14) N = N+ + e- – 1381.51 kJ/ mol (energy of ionization and dissociation – 14.22 eV) (15) H2↔2H – 434.95 kJ/ mol (energy of dissociation – 4.48 eV) (16)

N2↔2N – 948.54 kJ/ mol (energy of dissociation – 9.77 eV) (17)

**Figure 12.** Reactions, going in close proximity of the cathode space in a medium of ammonia, carbon dioxide and argon

On the basis of the above exposed data the following probable mechanism of carbonitriding in a saturating medium of ammonia and corgon could be suggested:

As the energy of dissociation and ionization of ammonia and carbon dioxide is higher, in the area of the cathode fall of the glow discharge probably atomic carbon should form initially by the reaction СО2+ + е- → С + О2 and atomic nitrogen by the reaction NH3+ = N + 3H. The dissociation of the ammonia molecule and the breakage of the carbon-oxygen bonds go close to the cathode in the zone of the negative glowing. Consequently, processes of ionization of the carbon (reaction СО2 + е- → СО2+ → С+ + 2О) and nitrogen (reaction NH3+ = N+ + 3H) atoms occur; these atoms impact the surface and diffuse at a certain distance into the material – [Fig.12]. The process of saturation of the metal surface depends only on the concentration of the atomic carbon and nitrogen in the plasma, as well as on the temperature of the article, while the electron or ion impact plays role for ensuring the necessary temperature of the details.

The availability of argon in the saturating medium in combination with CO2, leads to increasing the average energy in the discharge, which, at sufficient concentration of CO2, results in considerable reduction of the energy spent on the dissociation of a molecule.

In the process of carbonitriding part of the nitrogen atoms are replaced by the bigger carbon atoms, which causes forming the ε-phase in the carbonitrided layer. It is possible for two reasons: approximately the same ion radius of the nitrogen [rion = 13(5+1) pm, rion = 16(3+1) pm] and the carbon [rion = 16(4+1) pm]; the possibility for the carbon atoms to take up the vacant junctions.
