Possibilities of Additive Technologies for the Manufacturing of Tooling from Corrosion-Resistant Steels in Order to Protect Parts Surfaces from Thermochemical Treatment

: The structure and physical–mechanical properties of products made from powders of corrosion-resistant steel 12X18H10T by the laser-beam powder bed fusion (LB-PBF) and subsequent ion-plasma nitriding in the work were investigated. Comparative studies of the physical mechanical properties of specimens made by the LB-PBF and conventional method from steel of the same grade were carried out. The density of the specimens and the coefﬁcient of linear thermal expansion (CLTE) after the LB-PBF are almost the same as those of the conventionally manufactured specimens. Our analysis of the obtained dilatograms in the temperature range from 20 to 600 ◦ C showed that the CLTE of steel after the LB-PBF is within acceptable limits (18.6 × 10 − 6 1/ ◦ C). Their hardness, tensile strength, yield strength and elongation are higher than those of a conventionally manufactured specimen. The phase composition and structure of specimens of steel 12X18H10T made by the LB-PBF after the process of ion-plasma nitriding were investigated. The obtained results show that the mode of ion-plasma nitriding used in this case (stage 1—570 ◦ C for 36 h; stage 2—540 ◦ C for 12 h) does not lead to deterioration of the characteristics of the selected steel. A technological process for the manufacture of modiﬁed tooling from 12X18H10T steel by the LB-PBF was developed. It protects the surfaces that are not subject to nitriding and makes it possible to obtain a uniform high-quality nitrided layer on the working surface of the part made from spheroidal graphite iron.


Introduction
Additive manufacturing is defined as the process of coupling materials to create objects from 3D model data, layer by layer. It is opposed to "subtractive" manufacturing methods, such as traditional machining [1].
Additive manufacturing (AM) makes it possible to create products of complex shapes that cannot be manufactured by conventional methods. AM makes it possible to reduce the time between the drawing and the final product, reduce the production time of the product, reduce material consumption and shorten the technological cycle by reducing the number of operations. Nowadays, one of the most promising areas of AM is the manufacturing of products from metal powders by the laser beam powder bed fusion (LB-PBF) and direct metal deposition (DMD) [2][3][4][5]. The range of materials used is expanding, along with the widespread use of corrosion-resistant steels; research is underway to determine the optimal parameters for the manufacture of products such as ceramics, metal alloys and composite materials [6][7][8].
The authors of Reference [9] investigated the microstructure and electrochemical behavior of 316L steel processed by LB-PBF in a concentrated solution (0.9 M NaOH + 0.9% specimens after conventional quenching and low tempering. Investigated the influence of ultrasonic treatment and vibration tumbling on the surface quality of parts. It has been established that the use of ultrasonic treatment and vibration tumbling after LB-PBF allows us to improve the surface quality by reducing the roughness at the micro level and submicro level. The influence of the post-processing parameters on the mechanical characteristics of products manufactured by the LB-PBF method is determined to ensure the required properties of aerospace parts made of corrosion-resistant steels by the selective laser melting method.
The authors of Reference [8] consider shot blasting to reduce stresses and structural defects as a post-processing of specimens made of corrosion-resistant 316L steel by laser cladding. It is shown that the surface stress of the specimen formed by the hybrid process changed from tensile to compressive stress. At the same time, internal microdefects such as pores were reduced. The porosity of the specimen formed by the hybrid process was reduced by 90.12% than that of the laser cladding specimen, and the surface roughness decreased by 43.16%.
It is shown that in the process of the LB-PBF a finely dispersed structure is formed. That provides higher strength properties of steels after the LB-PBF than after conventional processing. The density of the specimens is at the similar level. The study of the effect of heat treatment on the mechanical characteristics of corrosion-resistant steels showed that the hardness of 20X13 steel specimens obtained by the LB-PBF is higher than that of a conventionally heat treated specimens. The wear resistance decreases with an increasing in the tempering temperature for all test specimens [22]. The authors of Reference [24] show that the grain size in specimens made using low power is smaller than in specimens made at higher power. The reason for it is that higher powers have a greater thermal effect on a larger melting pool. Specimens built by using lower power have a lower thermal gradient and slower cooling rate.
Despite the large number of different studies of corrosion-resistant steels obtained by the LB-PBF, a number of unsolved scientific and technological problems still remain. It affects the quality and cost of the products. Not enough attention is paid to the influence of thermal and thermochemical treatments on the products structure and properties. Research in this area is necessary to solve specific problems of using LB-PBF of corrosion-resistant steels in the engineering industry, particularly in the manufacture of various types of tooling. AM makes it possible to manufacture tooling for certain technological operations. For the manufacture of products that meet customer requirements, various types of tooling are used. The types of tooling are made for strictly defined operations. The use of additive technologies makes it possible to take into account the design features of the future tooling and design it strictly for a specific product. Currently, to increase the wear resistance of the parts, various types of thermal and thermochemical treatments are used; research is underway to develop new functional coatings with unique properties [25][26][27]. At the same time, there is a need to protect surfaces that are not subject to hardening. For this purpose, various methods are used, from special coatings to the manufacture of tooling. For example, it was used in the operations of ion-plasma nitriding. Specifically made equipment in the form of casings is used, and it covers certain surfaces from nitriding. The use of additive technologies makes it possible to manufacture special alloys tooling with specific complex shape. In this case, AM shows the maximum material utilization rate. Possibilities of using additive technologies for the manufacture of tooling from metal powders to protect the surfaces of parts from thermochemical treatment have received insufficient attention. It cannot be ruled out that the microstructure of products produced by the LB-PBF is exposed to saturating gases in a completely different way than the microstructure of products manufactured by conventional methods. There is a complex metal science task requiring a large number of experiments and studies on the effect of thermochemical treatment on the material made by AM.
The purpose of this work is to study the structure and physicomechanical properties of products made from domestically produced corrosion-resistant steel 12X18H10T powders by the LB-PBF and subsequent ion-plasma nitriding.

Materials and Methods
Corrosion-resistant chromium-nickel austenitic steel, grade X18H9T, was chosen as a material for the study. Metal powders of steel X18H9T (PRX18H9T, fraction from 20 to 63 µm) were prepared by AO "POLEMA" (Tula, Russia) by dispersing a molten metal by a jet of compressed gas. The choice of materials was determined by the request of aviation industry enterprises. It was used for the development of technological processes for the manufacture of tooling using AM. The paper investigates the possibility of replacing the conventional manufacturing technology of protective tooling by the production of nitrided parts with the LB-PBF technology.
In the work, the block part made from spheroidal graphite iron was considered. The flat end of the block was subjected to nitriding, while a number of surfaces were protected from nitrogen saturation. For this purpose, according to the conventional technology, tooling is made from steel 12X18H10T (Figure 1a). After ion-plasma nitriding, at the holes closed with balls, zones with a reduced hardness are formed ( Figure 1b). Such zones appear due to the shielding of the cast-iron surface by balls. To eliminate this problem and obtain a high-quality nitrided layer on the working surface of the block, it is proposed to modernize the design of the tooling and manufacture it by the LB-PBF. A 3D model of the upgraded tooling is shown in Figure 2. The non-nitriding holes are closed from below, thereby eliminating the shielding effect during the ion-plasma nitriding process. The advantage of the new tooling is a high material utilization rate, as well as ease of use. The operational requirements for the tooling are as follows: • The tooling geometry must provide a uniform nitriding layer on the block surface; the tooling components must cover the non-nitrided surfaces. The production goal was to design a structure and develop a manufacturing process using the LB-PBF method for protective tooling. The tooling protects blocks made from spheroidal graphite iron used in piston pumps for aircraft engines from ion-plasma nitriding in order to improve the quality of the nitrided layer. The goal was achieved by the completion of studies of the physical and mechanical properties of specimens made from corrosion-resistant steel 12X18H10T by laser-beam powder bed fusion. The chemical composition of spheroidal graphite iron is shown in Table 1. Block blank is nitrided by using conventional tooling to protect surfaces that are not subject to nitriding. Tooling made in a conventional way does not provide a sufficient quality of the nitrided layer on the surface of the part (Figure 1b).
The block diameters are closed with a casing (1) and a cover (2), and the holes are closed with balls (3). The part stands on a sheet (4) with a Ø 0.75 mm drilled hole for vacuum pumping. The casing, sheet and cover are made from steel 12X18H10T; the balls are made from steel IIIX15 (Figure 1a).
After ion-plasma nitriding, at the holes closed with balls, zones with a reduced hardness are formed (Figure 1b). Such zones appear due to the shielding of the cast-iron surface by balls. To eliminate this problem and obtain a high-quality nitrided layer on the working surface of the block, it is proposed to modernize the design of the tooling and manufacture it by the LB-PBF. A 3D model of the upgraded tooling is shown in Figure 2. After ion-plasma nitriding, at the holes closed with balls, zones with a reduced hardness are formed (Figure 1b). Such zones appear due to the shielding of the cast-iron surface by balls. To eliminate this problem and obtain a high-quality nitrided layer on the working surface of the block, it is proposed to modernize the design of the tooling and manufacture it by the LB-PBF. A 3D model of the upgraded tooling is shown in Figure 2. The non-nitriding holes are closed from below, thereby eliminating the shielding effect during the ion-plasma nitriding process. The advantage of the new tooling is a high material utilization rate, as well as ease of use. The operational requirements for the tooling are as follows: • The tooling geometry must provide a uniform nitriding layer on the block surface; the tooling components must cover the non-nitrided surfaces.

•
The chemical composition and microstructure of the steel must ensure the depth of the nitrided layer is no more than 1/2 of the wall thickness of the tooling for a long period of time (to increase the service life).

•
The nitrided layer, regardless of the service life, should not become embrittled.
The material for the tooling is austenitic steel 12X18H10T, since this steel is almost not prone to nitriding. The non-nitriding holes are closed from below, thereby eliminating the shielding effect during the ion-plasma nitriding process. The advantage of the new tooling is a high material utilization rate, as well as ease of use. The operational requirements for the tooling are as follows:

•
The tooling geometry must provide a uniform nitriding layer on the block surface; the tooling components must cover the non-nitrided surfaces.

•
The chemical composition and microstructure of the steel must ensure the depth of the nitrided layer is no more than 1/2 of the wall thickness of the tooling for a long period of time (to increase the service life).

•
The nitrided layer, regardless of the service life, should not become embrittled.
The material for the tooling is austenitic steel 12X18H10T, since this steel is almost not prone to nitriding.
Ion-plasma nitriding of blocks made from spheroidal graphite iron was carried out on an ELTROPULS H60/100 (ELTROPULS Anlagenbau GmbH, Baesweiler, Germany). Nitriding mode double-stage: 1st stage-570 • C, 36 h; 2nd stage-540 • C, 12 h. Before nitriding, cleaning is carried out in a hydrogen environment for 10 min at a temperature of 280 degrees and a pressure of 5 Pa.
Laser-beam powder bed fusion was carried out on an EOS M 280 (EOS GmbH, Krailling, Germany).
The granulometric analysis of the powders was carried out on an OCCHIO500nano image analyzer manufactured by OCCHIO SA (Belgium) by static image analysis, according to ISO 13322-1: 2014 [4,21]. Real-time chemical analysis and particle morphology were determined on a VEGA 3 LMH scanning electron microscope (TESCAN, Brno, Czech Republic).
The microstructure and microrelief of the steels surface were studied, using an optical microscope Carl Zeiss AxioObserver D1m (Carl Zeiss, Oberkochen, Germany) and an electron microscope Phenom ProX (Thermo Fisher Scientific, Waltham, MA, USA), in accordance with GOST 5639-82 and GOST 1583-93.
X-ray phase analysis was carried out on an X-ray machine for structural analysis ARL X'TRA (Thermo Fisher Scientific, Waltham, MA, USA) by scanning with X-ray according to the Bregg-Brentano method. An X-ray tube with a copper (CuK α ) anode was used to excite the characteristic spectrum. To record the diffraction pattern, a Si (Li) semiconductor detector was used, which suppresses the white radiation of the anode and the β-line of the X-ray tube spectrum in a ratio not worse than 1/300 with respect to Kα. The work of the machine is carried out by the WinXRD 2.0-8 control software and the ICDDPDF-2 reference radiographs database (2010). X-ray diffraction patterns were taken at a maximum goniometer radius of 520 mm, a tube current of 30 mA and an accelerating voltage of 40 kV. The horizontal collimation slits (limiting the vertical divergence of the X-ray beam) were 2 mm × 2 mm in size. When taking X-ray diffraction patterns, a continuous method of counter movement with an angular velocity of 1.0 • /min was used in the range of angles (10 • -120 • )-2Θ.
Measurements of the geometric parameters of the products were carried out on a multisensor coordinate measuring machine for high-precision measurements (WerthMesstechnik, Giessen, Germany); roughness measurements were performed on a profiler-profilometer (HommelTester T8000, Jena, Germany).
The density of the specimens was determined by hydrostatic weighing on a Mettler-Toledo XP504 balance with an accuracy of 0.001 g/cm 3 .
Gas porosity was determined on panoramic images with an area of 4 mm 2 , using a Carl Zeiss AxioObserver D1m optical microscope. Image processing was performed by using the ThixometPro program. The volume fraction of pores, their size distribution and the total porosity score were evaluated.
The INSTRON Electropuls E10000 testing system was used to measure tensile strength, yield strength and elongation.
The dilatometric analysis of LB-PBF-manufactured 12X18H10T steel specimens was carried out by using a LINSEIS L75H/1400 (LINSEIS, Selb, Germany) differential dilatometer. Dilatometric analysis was carried out in order to reveal changes in the Coefficient of Linear Thermal Expansion (CLTE) upon repeated heating from 20 to 600 • C. That specified parameter must be taken into account when determining the dimensions of the tooling.

Results and Discussion
The results of the granulometric and granulomorphological analysis show that the powder of steel 12X18H10T is characterized by a spherical particle shape with a small number of rod-shaped particles, high fluidity, microcrystalline structure, equiaxial morphology and a small number of satellites ( Figure 3). According to the obtained integral and differential histograms of the powder particle size distribution, it was concluded that the average particle size, dav is 33.25 μm. The particle size in the range of 0-45 μm is 82.35%, which follows from the results of Table 2. Thus, the analysis of PR-12X18H10T showed that the powder meets the requirements for powders for the LB-PBF. According to the obtained integral and differential histograms of the powder particle size distribution, it was concluded that the average particle size, d av is 33.25 µm. The particle size in the range of 0-45 µm is 82.35%, which follows from the results of Table 2. Thus, the analysis of PR-12X18H10T showed that the powder meets the requirements for powders for the LB-PBF. The modes for the manufacture of products from steel 12X18H10T by the LB-PBF were determined by using parametric analysis. Parametric analysis is based on varying process parameters. The main parameters affecting the quality of the manufactured specimens are the laser power, scanning speed, thickness of the powder layer and type of scanning strategy. The basic process mode for steel 12X18H10T is presented in Table 3. Table 3. LB-PBF process mode for the manufacture of products from steel 12X18H10T.

Parameters Value
Laser power, W 50 This mode for 12X18H10T powder makes it possible to obtain dense products with a minimum number of pores. The percentage of pores on the plane of the cross-section is 0.06-0.08%, which indicates a homogeneous material and complete penetration of the powder particles. Dual-zone scanning strategy allows us to produce products with a great isotropy of properties.
Comparative studies of the physical properties of the specimens made by the LB-PBF and conventionally manufactured ones of the same steel grade were carried out (Table 4). The density of the specimens and the CLTE after the LB-PBF are almost the same as the conventionally manufactured ones. The dilatometric analysis of steel 12X18H10T specimens was carried out by using a differential dilatometer. Analysis of the obtained dilatograms was carried out in the temperature range from 20 to 600 • C. It showed that the change in dimensions is within acceptable limits, which will ensure the stability of the dimensions of the tooling in the nitriding process. Temperature range of ion-plasma nitriding (first stage-570 • C 36 h; second stage-540 • C 12 h), which correlates with the results of previous studies [14].
To study the mechanical properties, the specimens were prepared according to the mode indicated in Table 3. Table 5 shows the comparative characteristics of the mechanical properties of specimens made by the LB-PBF and conventionally manufactured specimen of the same steel. The results of the study show that the hardness, tensile strength, yield strength and elongation are higher than those of a traditionally manufactured specimens, and these results are consistent with the data of Reference [28].
The phase composition and structure of specimens from steel 12X18H10T made by the LB-PBF method before and after the nitriding process were investigated (Figures 4-7). The phase composition and structure of specimens from steel 12X18H10T made by the LB-PBF method before and after the nitriding process were investigated (Figures 4-7). Figure 4 shows the microstructure of steel after the LB-PBF. The boundaries of the melt pools with an arcuate configuration are visible on the cross-section (Figure 4a). This is due to the Gaussian energy distribution of the laser beam. The direction of crystal growth in the central zone of the melt pool does not change significantly when crossing the boundary between the layers. There, epitaxial growth of the next layer on the previous one is possible.
Boundaries are observed both between the melt pools (oval configuration) and between the tracks in the longitudinal cross-section (Figure 4b). Accumulations of carbides are visible as a result of thermal cycling near the boundaries of the melt pools and at the boundaries between the tracks. After quenching from the liquid state, which occurs during the crystallization of the melt pool, tempering occurs at different temperatures while reheating. The tempering temperature depends on the distance from the heating source. The structure of the steel before heat treatment (i.e., immediately after fabrication by the LB-PBF method) is γ-Fe and α-Fe; the intermetallic compound FeNi, iron carbide Fe3C and FeO oxide are also formed in steel by the LB-PBF method.
Two-stage nitriding of steel (first stage-570 °C for 36 h; second stage-540 °C for 12 h (nitriding mode for spheroidal graphite iron)) showed that the depth of the nitrided layer on the specimen made by the LB-PBF method is less than on the specimens obtained by the conventional method ( Figure 5). That is explained by the more dispersed structure of steel after the LB-PBF.  The phase composition and structure of specimens from steel 12X18H10T made by the LB-PBF method before and after the nitriding process were investigated (Figures 4-7). Figure 4 shows the microstructure of steel after the LB-PBF. The boundaries of the melt pools with an arcuate configuration are visible on the cross-section (Figure 4a). This is due to the Gaussian energy distribution of the laser beam. The direction of crystal growth in the central zone of the melt pool does not change significantly when crossing the boundary between the layers. There, epitaxial growth of the next layer on the previous one is possible.
Boundaries are observed both between the melt pools (oval configuration) and between the tracks in the longitudinal cross-section (Figure 4b). Accumulations of carbides are visible as a result of thermal cycling near the boundaries of the melt pools and at the boundaries between the tracks. After quenching from the liquid state, which occurs during the crystallization of the melt pool, tempering occurs at different temperatures while reheating. The tempering temperature depends on the distance from the heating source.  The structure of the steel before heat treatment (i.e., immediately after fabrication by the LB-PBF method) is γ-Fe and α-Fe; the intermetallic compound FeNi, iron carbide Fe3C and FeO oxide are also formed in steel by the LB-PBF method.
Two-stage nitriding of steel (first stage-570 °C for 36 h; second stage-540 °C for 12 h (nitriding mode for spheroidal graphite iron)) showed that the depth of the nitrided layer on the specimen made by the LB-PBF method is less than on the specimens obtained by the conventional method ( Figure 5). That is explained by the more dispersed structure of steel after the LB-PBF.  The phase analysis of the nitrided layer on 12X18H10T steel LB-PBF specimens and conventionally manufactured specimens shows that, in both cases, a nitride zone is formed, which is a single-phase region of the γ′-phase of Fe4N, γ-solid solution of nitrogen in austenite and chromium nitrides CrN ( Figure 6). Our analysis of the microstructure of the core of a nitrided LB-PBF specimen from 12X18H10T steel (Figure 7) showed that annealing that occurs during nitriding leads to the blurring of the boundaries of the melt pools and the formation of a structure characteristic of austenitic steels-polyhedral grains. Thus, studies of the microstructure of specimens made from 12X18H10T steel and subjected to nitriding will not lead to the embrittlement of the layer on the tooling made by the LB-PBF. The structure of the core improves, as a result of annealing at 580 °C, the texture, leading to decreases in the anisotropy of properties and residual stresses. The obtained results show that the selected mode of ion-plasma nitriding (first stage-570 °C for 36 h; second stage-540 °C for 12 h) will not lead to the deterioration of the characteristics of the selected steel.
The kinetics of the depth growth of nitrided layers and the change in hardness on steel 12X18H10T were studied.
The diffusion of nitrogen into steel is extremely difficult, due to the predominant amount of the γ-phase and the dense chromium oxide film. However, this steel is nitrided by the ion-plasma method, due to cathodic sputtering in hydrogen or argon, in order to remove the oxide film, and the so-called "bombardment" of nitrogen atoms into the steel, formed, which is a single-phase region of the γ′-phase of Fe4N, γ-solid solution of nitrogen in austenite and chromium nitrides CrN ( Figure 6). Our analysis of the microstructure of the core of a nitrided LB-PBF specimen from 12X18H10T steel (Figure 7) showed that annealing that occurs during nitriding leads to the blurring of the boundaries of the melt pools and the formation of a structure characteristic of austenitic steels-polyhedral grains. Thus, studies of the microstructure of specimens made from 12X18H10T steel and subjected to nitriding will not lead to the embrittlement of the layer on the tooling made by the LB-PBF. The structure of the core improves, as a result of annealing at 580 °C, the texture, leading to decreases in the anisotropy of properties and residual stresses. The obtained results show that the selected mode of ion-plasma nitriding (first stage-570 °C for 36 h; second stage-540 °C for 12 h) will not lead to the deterioration of the characteristics of the selected steel.
The kinetics of the depth growth of nitrided layers and the change in hardness on steel 12X18H10T were studied.
The diffusion of nitrogen into steel is extremely difficult, due to the predominant amount of the γ-phase and the dense chromium oxide film. However, this steel is nitrided by the ion-plasma method, due to cathodic sputtering in hydrogen or argon, in order to remove the oxide film, and the so-called "bombardment" of nitrogen atoms into the steel,   (Figure 4a). This is due to the Gaussian energy distribution of the laser beam. The direction of crystal growth in the central zone of the melt pool does not change significantly when crossing the boundary between the layers. There, epitaxial growth of the next layer on the previous one is possible.
Boundaries are observed both between the melt pools (oval configuration) and between the tracks in the longitudinal cross-section (Figure 4b). Accumulations of carbides are visible as a result of thermal cycling near the boundaries of the melt pools and at the boundaries between the tracks. After quenching from the liquid state, which occurs during the crystallization of the melt pool, tempering occurs at different temperatures while reheating. The tempering temperature depends on the distance from the heating source.
The structure of the steel before heat treatment (i.e., immediately after fabrication by the LB-PBF method) is γ-Fe and α-Fe; the intermetallic compound FeNi, iron carbide Fe3C and FeO oxide are also formed in steel by the LB-PBF method.
Two-stage nitriding of steel (first stage-570 • C for 36 h; second stage-540 • C for 12 h (nitriding mode for spheroidal graphite iron)) showed that the depth of the nitrided layer on the specimen made by the LB-PBF method is less than on the specimens obtained by the conventional method ( Figure 5). That is explained by the more dispersed structure of steel after the LB-PBF.
The phase analysis of the nitrided layer on 12X18H10T steel LB-PBF specimens and conventionally manufactured specimens shows that, in both cases, a nitride zone is formed, which is a single-phase region of the γ -phase of Fe 4 N, γ-solid solution of nitrogen in austenite and chromium nitrides CrN ( Figure 6).
Our analysis of the microstructure of the core of a nitrided LB-PBF specimen from 12X18H10T steel (Figure 7) showed that annealing that occurs during nitriding leads to the blurring of the boundaries of the melt pools and the formation of a structure characteristic of austenitic steels-polyhedral grains.
Thus, studies of the microstructure of specimens made from 12X18H10T steel and subjected to nitriding will not lead to the embrittlement of the layer on the tooling made by the LB-PBF. The structure of the core improves, as a result of annealing at 580 • C, the texture, leading to decreases in the anisotropy of properties and residual stresses. The obtained results show that the selected mode of ion-plasma nitriding (first stage-570 • C for 36 h; second stage-540 • C for 12 h) will not lead to the deterioration of the characteristics of the selected steel.
The kinetics of the depth growth of nitrided layers and the change in hardness on steel 12X18H10T were studied.
The diffusion of nitrogen into steel is extremely difficult, due to the predominant amount of the γ-phase and the dense chromium oxide film. However, this steel is nitrided by the ion-plasma method, due to cathodic sputtering in hydrogen or argon, in order to remove the oxide film, and the so-called "bombardment" of nitrogen atoms into the steel, due to which the diffusion process proceeds faster. For the experiments, we used specimens made by the LB-PBF and the conventional process. The specimens were subjected to fivefold nitriding in a two-stage mode: first stage-570 • C for 36 h; second stage-540 • C for 12 h (nitriding mode for spheroidal graphite iron). The results of the dependence of the depth of the nitrided layer on time are shown in Figure 8a, the hardness in Figure 8b, (blue line-depth of the layer on the conventionally manufactured specimens, red line-for the specimens made by the LB-PBF). Nitrogen diffusion, in both cases, proceeds in accordance with Fick's first law: = − , where J is the diffusion flux, D is the diffusion coefficient and is the concentration gradient. There is a sharp increase in depth in 144 h to 0.26 mm on the plot of the nitrided layer depth dependence on time, and then the process slows down and goes to a depth of no more than 0.27 mm.
For the LB-PBF specimen, the diffusion of nitrogen into the depth of the metal is noticeably slower. The hardness of the layer is insignificantly higher than for the conventionally manufactured specimen. It is probably caused by the finer structure of the LB-PBF specimen.
According to the selected modes (Table 3), and in accordance with the developed model (Figure 2), the equipment was made from 12X18H10T steel by the LB-PBF. The benefit of the modified tooling is to reduce the number of elements (from 13 to 4). In addition, it serves to improve the quality of the nitrided layer on the working surface of the block part made from spheroidal graphite iron. The tooling consists of a monolithic casing Nitrogen diffusion, in both cases, proceeds in accordance with Fick's first law: J = −D ∂C ∂x , where J is the diffusion flux, D is the diffusion coefficient and ∂C ∂x is the concentration gradient. There is a sharp increase in depth in 144 h to 0.26 mm on the plot of the nitrided layer depth dependence on time, and then the process slows down and goes to a depth of no more than 0.27 mm.
For the LB-PBF specimen, the diffusion of nitrogen into the depth of the metal is noticeably slower. The hardness of the layer is insignificantly higher than for the conventionally manufactured specimen. It is probably caused by the finer structure of the LB-PBF specimen.
According to the selected modes (Table 3), and in accordance with the developed model (Figure 2), the equipment was made from 12X18H10T steel by the LB-PBF. The benefit of the modified tooling is to reduce the number of elements (from 13 to 4). In addition, it serves to improve the quality of the nitrided layer on the working surface of the block part made from spheroidal graphite iron. The tooling consists of a monolithic casing with thin-walled bushings, and two thin-walled covers covering the small outer and central inner diameters (Figure 9). An improvement in the quality of the nitrided layer is ensured by replacing the balls covering the non-nitrided holes with thin-walled bushings (Figure 9). Non-nitrided holes are closed from below, thereby eliminating the effect of shielding the spheroidal graphite iron surface by balls during the process of ion-plasma nitriding ( Figure 10). As a result of shielding, a zone of local overheating appears, leading to a structural defect. The defect is the appearance of a zone of nitrogenous ferrite on the surface of the layer, which has a low hardness of 397-454 HV (Figure 10a). Comparative studies of the elemental composition in the surface zones of the defective layer ( Figure 10) and in a similar area of the nondefective layer corresponding to the requirements of the technological process ( Figure 11) by the method of energy dispersive spectroscopy (EDS) showed a decrease in the concentration of nitrogen and carbon in the defective layer.  An improvement in the quality of the nitrided layer is ensured by replacing the balls covering the non-nitrided holes with thin-walled bushings (Figure 9). Non-nitrided holes are closed from below, thereby eliminating the effect of shielding the spheroidal graphite iron surface by balls during the process of ion-plasma nitriding ( Figure 10). As a result of shielding, a zone of local overheating appears, leading to a structural defect. The defect is the appearance of a zone of nitrogenous ferrite on the surface of the layer, which has a low hardness of 397-454 HV (Figure 10a). Comparative studies of the elemental composition in the surface zones of the defective layer ( Figure 10) and in a similar area of the non-defective layer corresponding to the requirements of the technological process ( Figure 11) by the method of energy dispersive spectroscopy (EDS) showed a decrease in the concentration of nitrogen and carbon in the defective layer. An improvement in the quality of the nitrided layer is ensured by replacing the balls covering the non-nitrided holes with thin-walled bushings (Figure 9). Non-nitrided holes are closed from below, thereby eliminating the effect of shielding the spheroidal graphite iron surface by balls during the process of ion-plasma nitriding ( Figure 10). As a result of shielding, a zone of local overheating appears, leading to a structural defect. The defect is the appearance of a zone of nitrogenous ferrite on the surface of the layer, which has a low hardness of 397-454 HV (Figure 10a). Comparative studies of the elemental composition in the surface zones of the defective layer ( Figure 10) and in a similar area of the nondefective layer corresponding to the requirements of the technological process ( Figure 11) by the method of energy dispersive spectroscopy (EDS) showed a decrease in the concentration of nitrogen and carbon in the defective layer.  The use of modified tooling made by the LB-PBF from austenitic corrosion-resistant steel 12X18H10T (analogue of AISI 321) allows us to obtain a high-quality nitrided layer on the surface of the block part made from spheroidal graphite iron.

Conclusions
A technological process for the modified tooling manufacturing by the LB-PBF from 12X18H10T steel powder (analogue of AISI 321) was developed. Modified tooling protects certain surfaces of the part that are not subject to nitriding. That allows us to obtain a uniform high-quality nitrided layer on the working surface of the part made from spheroidal graphite iron. The proposed technology provides the required performance characteristics of the tooling.
Research confirms the fact that steel has good dimensional stability. The temperature coefficient of linear expansion of steel after the LB-PBF is within acceptable limits (18.6 × 10 −6 1/°C). Phase-transition γ↔α does not occur in the temperature range 500-600 °C (nitriding temperature range). Tooling made from austenitic steel withstands long-term operation and multiple usage. That is shown by studies of the kinetics of the nitrided layers' depth growth and the change in hardness on steel 12X18H10T in the process of ion-plasma nitriding. The results of the studies show that protective tooling made from steel 12X18H10T can be used industrially for the surfaces of spheroidal graphite iron blocks used in piston pumps of aircraft engines in order to improve the quality of the nitrided layer.

Conclusions
A technological process for the modified tooling manufacturing by the LB-PBF from 12X18H10T steel powder (analogue of AISI 321) was developed. Modified tooling protects certain surfaces of the part that are not subject to nitriding. That allows us to obtain a uniform high-quality nitrided layer on the working surface of the part made from spheroidal graphite iron. The proposed technology provides the required performance characteristics of the tooling.
Research confirms the fact that steel has good dimensional stability. The temperature coefficient of linear expansion of steel after the LB-PBF is within acceptable limits (18.6 × 10 −6 1/ • C). Phase-transition γ↔α does not occur in the temperature range 500-600 • C (nitriding temperature range). Tooling made from austenitic steel withstands long-term operation and multiple usage. That is shown by studies of the kinetics of the nitrided layers' depth growth and the change in hardness on steel 12X18H10T in the process of ion-plasma nitriding. The results of the studies show that protective tooling made from steel 12X18H10T can be used industrially for the surfaces of spheroidal graphite iron blocks used in piston pumps of aircraft engines in order to improve the quality of the nitrided layer.