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Mechanical behaviour of austenitic stainless steel loaded in the aqueous solution of H2SO4 during tensile testing
Amar Abbouba, Ahmed Abourab,
Mokhtar Belkaceme, Djameleddine Semsoumf
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uj a Mustapha Stambouli University, Faculty of Sciences and Technology, E Department of Mechanical Engineering, q Mascara, People's Democratic Republic of Algeria, O e-mail: [email protected], corresponding author, ^ ORCIDiD: https://orcid.org/0009-0004-0158-5837
— b Ahmed Zabana University, Faculty of Sciences and Technology,
H Department of Mechanical Engineering,
^ Relizane, People's Democratic Republic of Algeria,
e-mail: ahmed.aboura @univ-relizane.dz, ORCID iD: https://orcid.org/0009-0005-3509-2026 c Mustapha Stambouli University, Faculty of Sciences and Technology, Department of Civil Engineering,
Laboratory for the Study of Structures and Mechanics of Materials, Mascara, People's Democratic Republic of Algeria, e-mail: [email protected], < ORCIDiD: https://orcid.org/0000-0002-8244-5817
O d Mustapha Stambouli University, Faculty of Sciences and Technology,
KI Department of Civil Engineering,
Laboratory for the Study of Structures and Mechanics of Materials, Mascara, People's Democratic Republic of Algeria, w e-mail: [email protected],
ORCID iD: https://orcid.org/0009-0008-2314-9402
e Mustapha Stambouli University, Faculty of Sciences and Technology, Department of Mechanical Engineering, ^ Mascara, People's Democratic Republic of Algeria,
e-mail: [email protected], ORCID iD: https://orcid.org/0009-0004-2533-9622 Mustapha Stambouli University, Faculty of Sciences and Technology, Department of Mechanical Engineering, Mascara, People's Democratic Republic of Algeria, e-mail: [email protected], ORCID iD: https://orcid.org/0009-0009-8304-9072
doi https://d0i.0rg/l 0.5937/vojtehg72-49964
ACKNOWLEDGMENTS: This research was supported by the General Directorate of Scientific Research and Technological Development of Algeria (DGRSDT: Under the authority of the Ministry of Higher Education and Scientific Research in charge of scientific research).
FIELD: materials
ARTICLE TYPE: original scientific paper Abstract:
Introduction/purpose: Stainless steels have excellent corrosion resistance and adequate mechanical properties. However, their use in aggressively hydrogenated environments in the energy industry causes a loss of ductility. This work studied the effect of hydrogen on the mechanical behavior of the DINX15CrNiSi25.21/AISI310 austenitic stainless steel loaded in an aqueous solution of purely sulfuric acid H2SO4 at 1N at room temperature during tensile testing.
Methods: Experimental characterization techniques are applied to standardised machining-manufactured tensile specimens which underwent w a series of heat treatments ranging from quenching at 1050°C for35 minutes to tempering at 680°C for 30 minutes. This is accompanied by a succession of immersions of these samples by cryogenic quenching cycles at -196°C for a duration of 1 hour. The hydrogen was electrolytically loaded in a Pyrex glass cell for various loading times, ranging from 1h00 to 15h00, with a step of 2h00.
Results: The results showed a reduction in mechanical properties and plasticity. The electrochemical method confirmed the material's sensitivity to hydrogen embrittlement, calculating the embrittlement criterion EI (%). This method indicates a rapid increase in values depending on hydrogen loading times, with a maximum value of 41.60%.
Conclusion: The study highlights the negative impact of hydrogen on the mechanical properties of AISI310 stainless steel, emphasising the need for reduced hydrogen exposure in steel applications.
Key words: austenitic stainless steel, heat treatments, hydrogen preloaded, mechanical properties, hydrogen embrittlement (HE), faces.
Introduction
The ORSIM Oued Rhiou production unit employs the AISI310 series of austenitic stainless steel. These materials are refractory and are well-known for their categories of ferritic-austenitic steel. They contain 25% chromium and 21% nickel as additional elements. Chemical industry, petrochemicals, and energy sectors, including offshore wind turbines, highly recommend these alloys for their superior corrosion resistance due to their crystalline structure and high tensile strength, surpassing 950 MPa (Chauveau & Aubry, 2008). Working conditions in aggressive environments may require high percentages of chromium, nickel, and molybdenum to improve corrosion resistance. Several authors have
conducted laboratory tests to study the electrochemical corrosion of this alloy (Chauveau & Aubry, 2008; Brass et al, 2000).
Other authors (Bach, 2018; Chêne, 2009; Brass et al, 2000) have studied the mechanical behaviour of these steels in relation to pitting | corrosion, temperatures, and hydrogen embrittlement (the phenomenon of the absorption of the hydrogen molecule inside the crystal lattice) during 202 exposure to different media, including gases, liquids, and high cc temperatures. Recently, several in-depth studies (Sales, 2015; Bach, 2018; Grimault et al, 2012; Lo et al, 2009; Iacoviello, 1995; Matsui et al, 1979) have been published on the mechanism of hydrogen embrittlement o (H.E). These studies examine how the methods and protocols used in
< industrial cathodic loading conditions lead to a reduction in ductility. The CI studies aim to determine the appropriate medium, concentration, and pre-
charging time in hours while fixing the current intensity (Hamissi et al, 2016).
£ This experiment aims to fully penetrate the hydrogen molecule (H2),
< similar to the work of other authors ( Laureys et al, 2020; Cauwels et al, 2020; Robertson et al, 2015; Kittel et al, 2013; Lynch, 2012; Depover et al, 2014), in order to make a comparison using the experimental curves obtained in tensile tests (Grimault et al, 2012; He et al, 1999; Smanio et
w al, 2008) at slow strain rates in the interest of looking at and analysing the GLA performance of mechanical characteristics and ductility from the point of view of their service conditions, application, and operation.
Experimental work
Materials
Chemical composition
The chemical composition of the stainless steel duplex, type X15CrNiSi25.21/AISI310, is represented in mass percentage in Table 1.
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Table 1 - Weight (%) of the AISI310 chemical composition
Fe% C% Cr% Ni% Si% Mn%
52,201 0.057 25,23 21.08 1,712 1.013
P% S% NB% Mo% Al% Co%
<0.0003 0.052 0.035 0.204 0.041 0.103
B% V% Ti% Cu% W% Pb%
0.005 0.124 0.035 0.176 0.011 0.052
Tensile test specimens
The tensile specimens used in this experimental part are cylindrical (Figure 1) and obtained by machining according to DIN50125 Standard using a semi-automatic (TSA) lathe of the reference: Oerlikon—Buhrle.SA, Switzerland Type: DEOa.
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Figure 1 - Geometric shape and dimensions of the used tensile specimens
Mechanical characteristics
A mechanical tensile fracture test was carried out on a standardized reference test specimen in order to obtain the desired initial mechanical characteristics in the raw state without heat treatment (see Table 2).
- The method used for this test is mechanical fracture by traction using a Frank Karl GMBH traction machine, with a constant applied load of Pmax= 400 kN and a slow deformation speed of (£ =2.7x10-6 S-1),
- The elongation (A) is measured as percentage (%), according to the equation:
A (%) = (A-A0)/A0 x100 (%).
- The aim is to obtain the mechanical properties in the initial state (raw and without thermal treatment).
Table 2 - Initial mechanical characteristics of the AISI310 austenitic stainless steel
studied
Initial mechanical characteristics
am ae ar Z A
Material (Air) (Air) (Air) (Air) (Air)
(MPa) (MPa) (MPa) (%) (%)
AISI310
Reference
(Air)
750.0
720.0
542.0 68.60% 24.10%
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Heat treatments (quenching, tempering)
After the manufacture of the tensile specimens, they undergo an austenization heat treatment cycle, see (Figure 2), which first consists of heating the specimens for 35 minutes at 1050°C followed by rapid quenching in water. This treatment can be followed by tempering at a temperature of 680°C for 30 minutes, then cooling in the open air (Poupeau, 1981; Sassoulas, 1997; Kenfack, 2015). Tempering makes it possible to eliminate the surface tensions developed during quenching. After these heat treatments, the material is perfectly homogeneous with a stable austenite and a relaxation of internal residual stresses, which leads to an increase in the yield strength (ae) (Grimault et al, 2012; Barralis et al, 1999).
Cycle (Quenching, Tempering)
-Quenching at
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Tempering at 680°C/30min
Open air cooling
50 100
Heat treatment time in minutes.
150
Figure 2 - Cycle of the heat treatment applied
Cryogenic heat treatment at -196°C
The next step consists of heat treating all the test specimens by cryogenic quenching at -196°C by immersion in a liquid nitrogen (N2) bath for a holding time of 1 hour prior to heating in the open air for 40 minutes (see Figure 3).
The number of cycles is repeated in succession up to fifteen cycles (Aurélie Laureys et al, 2020; Cauwels et al, 2020; Robertson et al, 2015; Kenfack, 2015).
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Cryogenic heat treatment time in minutes.
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Figure 3 - Cycles of the applied cryogenic heat treatment at-196°C
Cathodic loading conditions of the test specimens
At room temperature ±20°C, the test specimens underwent cathodic loading by the aqueous solution of purely sulfuric acid H2SO4 at1N (Laureys et al, 2020; Cauwels et al, 2020; Robertson et al, 2015) using a Pyrex glass enclosure (see Figure 4). Galvanostatique charge by two electrodes (cathode and anode) was carried out under the conditions adopted:
• The applied cathodic current density is fixed at 100(mA/cm2).
• With an amperage of 1.5A, the hydrogen charging times are varied from 1 hour to 15 hours with a step of 2 hours.
Figure 4 - Pyrex cell of cathodic loading in the aqueous solution of sulfuric acid H2SO4 at
1N
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Mechanical fracture tensile test
After the electrolytic loading protocol (hydrogenated), all the specimens of the steel studied underwent a machine test by fracture using a reference tensile machine: Frank Karl GMBH, type: 83431 - Work Nr: 10650 (Figure 5 (a) and (b)). The fracture tests are carried out according to industrial conditions: the displacement nominal speed is £: 2.7x10-6S-1 (Cauwels et al, 2020) which corresponded to a constant applied load of 400kN. The mechanical results are recorded for analysis and construction of experimental curves (see Figures 6, 7 and 8).
(a) (b)
Figure 5 - (a), (b) Tensile machine Karl frank GMBH used
Table 3 shows the results of the mechanical properties following the fracture testing of all specimens before (specimen Reference) (Air) and after (specimen's hydrogenated) electrolytic pre-loading with hydrogen at room temperature ±20°C.
Table 3 - Mechanical properties of the AISI310 austenitic stainless steel after cathodic loading Mechanical properties after hydrogenated
N° specimen Hydrogen am(H) ae(H) ar(H) Z(H) A(H)
Loaded
in hours (MPa) (MPa) (MPa) (%) (%)
N°1 1hour 552 252 465 53% 21%
N°2 3hours 538 227 375 52% 20%
N°3 5hours 526 224 355 52% 19%
N°4 7hours 523 240 375 51% 18%
N°5 9hours 535 235 372 51% 17%
N°6 11hours 526 226 354 50% 16%
N°7 13hours 516 215 340 51% 15%
N°8 15hours 508 212 374 51% 14%
Embrittlement index EI (%)
The embrittlement index (EI) is calculated in the result part and discussion by relationship (l), which compares the lengths of an uncharged reference sample (Ao) and those of the other samples that are pre-charged (Ah) electrolytically by hydrogen. The weakening index leads to a loss of plasticity which translates into a reduction in the elongation A (%).
EI=(Ao(Air)-A(H)) /(Ao(Air)) x100(%). (1)
where
• Ao is the elongations specimen with no charge (air),
• Ah is the elongation specimen charged in hydrogen.
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Results and discussion
The results of the mechanical properties obtained are represented by experimental charts in Figures 6, 7 and 8. These charts show tensile strength, yield strength and failure strength.
The resistance of the steel results in a slight decrease in tensile strength, with a reduction of 26.40% observed at the shortest hydrogen loading time. As the loading time is extended, the tensile strength decreases further, reaching 26.67% at the longest loading time.
It was also observed that the failure strength of this type of material increased by 14.20 % during short loading times, reaching a value of 31.18 % following the hydrogen loading time until 15 hours (see Figure 6 and Table 3).
Figure 6 - Effect of the hydrogen loading time on the stress, the failure, and the yield strength in MPa of the AISI310 austenitic stainless steel
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Variation of plasticity A, Z (%)
Figure 7 represents the variation of the plasticity characteristics of the X15CrNiSi25.21/AISI310 steel influenced by hydrogen loading, which causes slight reductions in these Z (%) restrictions compared to the reference from Z(Air): 68.60 % to Z(H): 53.0 % to reach a stable value of Z(H): 51.0 % throughout the level of hydrogen pre-charging times in hours (Table 3).
Losses of its plasticity are explained by a progressive decrease in elongations A (%) in percentage compared to the reference, from A(Air): 24.10 (%) to A(H): 21.0 (%) until reaching a minimum value of its plasticity of A(H): 14.0 % (see Table 3). These results are similar to the work by (Hamissi et al, 2016) which shows losses of plasticity translating into a gradual reduction at the lengths A %, under the industrial conditions adopted (simulated medium, loading time in hours, high concentration)
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A(%) - Z (%)
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24,10 „„ „^21 20 19 18 17 16 15 14
0 1 3 5 7 9 11 13 15 Hydrogen loading time in hours.
Figure 7 - Effect of the hydrogen loading time on the variation of plasticity in (%) of the AISI310austenitic stainless steel
Yield strength oe (MPa)
Figure 8 shows a progressive reduction in the yield strength (oe) of the material studied compared to the reference under the usual atmosphere of oe(Air): 720.0 (MPa), to that under a high concentration of hydrogen oe(H): 252.0 (MPa). The yield strength passes through a
minimum value after the loading level of 15hours, oe(H): 212.0 (MPa), due to high solubility of bound hydrogen to industrial conditions: high current density, charging time in hours and significant mechanical stress. It allows the absorption of a significant quantity of hydrogen, which causes the embrittlement of the material. The phenomenon of hydrogen embrittlement (H.E) was studied by several authors (Brass et al, 2000). In the same direction, one can note a plastic deformation of the useful part of the specimen exerted by the applied tensile stress (Lo et al, 2009), which leads to the conclusion that this type of steel has a fragile behavior with a reduction in ductility and its yield strength by producing an internal cracking structure, see Figure 10 (a) and (b).
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Figure 8 - Effect of the hydrogen loading time on the yield strength (oe) in (MPa) of the AISI310 austenitic stainless steel
Hardness HRV (N/mm2)
Table 4 presents the results of the evolution hardness which changes the level of loading time in hours. It was noticed that the reference specimen presents the greatest value in HRV(Air) of the order 246.0 (N/mm2) in relation to the other test specimens which are pre-loaded during ifferent hydrogen cathodic charging times of the order HRV(H) of 175.0 (N/mm2), where the hardness HRV passing through a minimum HRV hardness is of the order HRV(H): 140.0 (N/mm2).
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Table 4 - Evolution hardness HRV of the AISI310 austenitic stainless steel after cathodic
loading
Hydrogen loading in hours Values of hardness HRV(30) (N/mm2)
Reference0 (Air) 246.00
1 hour 175.00
3 hours 170.00
5 hours 160.00
7 hours 160.00
9 hours 170.00
11 hours 150.00
13 hours 165.00
15 hours 140.00
Embrittlement index EI (%
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Table 5 shows the results of the embrittlement index (EI, in %) of this specimen, obtained by the cathodic method. This index corresponds to the loss of mechanical properties, in particular plasticity, and is deduced from the measured elongations.
The samples preloaded with hydrogen, A(H), were compared with a non-hydrogenated reference specimen, A0(Air). No additional loading was carried out after the mechanical tensile tests. The values of the embrittlement index are calculated according to formula (1) (Lo et al, 2009; Brass et al, 2000).
From formula (1), it was concluded that the hydrogen embrittlement index (EI, in %) values are irreversible (see Table 5).
The results show a significant increase in EI, from 0.0% for the Ao(Air) reference to 12.50% for the A(h) samples after a hydrogen loading time of up to 15hours. This rapid increase continues, reaching an embrittlement index EI(H) of 41.60%, validated by the work of M. Cauwels (Cauwels et al, 2020)
Table 5 - Embrittlement Index EI (%) of the AISI310 austenitic stainless steel
Hydrogen loading in hours Values of the Embrittlement Index EI (%)
Reference0 (Air) 0.00%
1 hour 12.50%
3 hours 16.60%
5 hours 20.80%
7 hours 25.10%
9 hours 29.10%
11 hours 33.30%
13 hours 37.50%
15 hours 41.60%
Specimen states faces
Other experimental work by the authors ( Smanio et al, 2008; Laureys et al, 2020; Kittel et al, 2013) was based on observations. The cracking of the test specimen types of the useful part subjected to fracture by tensile testing was observed in order to distinguish and validate the type of cracking which is linked to the zones of localized fractures (1) and (2). For further details, please refer to Figures 9 and 10.
The experimental study enables a comparison of the two examples of faces of the reference test specimens (Reference 0) of the useful part in the raw state and before the heat treatment. In Figure 9, face 1 (a) and face 2 (b) illustrate the aspects of specimen N°8 which underwent all the heat treatment applied, being electrolytically charged for 15 hours. A mechanical fracture tensile test was then carried out on the specimen at slow nominal speed, as illustrated in Figure 10, face 1 (a) and face 2 (b).
Face 1 (a) Face 2 (b)
Figure 9 - Faces of the specimen raw states (a): raw state Face 1; (b): raw state Face 2 of the AISI310 austenitic stainless steel
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Figures 10 (a) and 10 (b) show the evolution of two brittle fracture surfaces of a specimen loaded with hydrogen for 15 hours. These figures easily identify cracks after the mechanical tensile test, which generally results in a reduction in ductility and the capacity to support cyclic loads. This reduction is associated with the cleavage of the weakened (a) ferrite (Philibert et al, 2013) and the ductile fracture of austenite (y).
Internal cracks are typically observed at both ends of this tensile test specimen; these are continuous cracks propagating over the entire fractured zone within the grain boundaries (Laureys et al, 2020; Lo et al, 2009) of the ferrite phase (inter-granular cracking) (Brass et al, 2000). The crack is broken at an angle of 90° with the axis of the applied stress load (Kittel et al, 2013; Smanio et al, 2008).
Hydrogen promotes trans-granular cracking of the ferrite phase, including the indices of micro-cracks in the austenitic phase, which is validated by a previous study (Lo et al, 2009).
Face 1 (a)
Face 2 (b)
Figure 10 - Specimen faces (a): facel, (b): face 2 - fractured specimen (propagation of cracking after hydrogenation at 15hours of sulfuric acid H2SO4 at 1N of the AISI310
austenitic stainless steel
Conclusion
The objective of this study was to characterise experimentally the influence of electrolytic hydrogen on the mechanical characteristics of AISI310 austenitic stainless steel. The remarks that can be made from this study are given as follows:
• The variation in tensile strength, yield strength, and failure strength of austenitic stainless steel decreases significantly with the increase in the duration of hydrogen loading, with reductions of 32.26%, 70.55%, and 30.99%, respectively. This can be
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explained by the fact that hydrogen diffusing into the steel's atomic lattice in the form of (H+) weakens the metallic bond, reducing resistance until the material breaks.
• The structure of steel plays a very important role in the diffusion of hydrogen. The variation in mechanical resistance between the initial, untreated material and the hydrogen-charged material demonstrates this. This variation in resistance is pronounced by the variation in the hydrogen charging time as well as the temperature.
• The phenomenon of hydrogen embrittlement is more pronounced under high concentrations of hydrogen produced by industrial polarization conditions (charging time in hours, high current density, high acid concentration); this is because the martensitic pseudo-transformation makes the material harder and therefore more fragile.
• The mechanical tensile tests, which are related to the damage index EI (%), show that the absorbed hydrogen causes the elongation to decrease at break and creates a difference in elongation between the specimens that are loaded and those that are not loaded. High loading times produce a maximum value of the embrittlement index equal to EI=41.60(%).
• AISI310 stainless steel experiences strength reduction and embrittlement with increased hydrogen exposure, requiring minimized exposure, alternative material selection, and design considerations for hydrogen environments. Engineers should make informed decisions for safety and longevity of structures when using AISI310 stainless steel.
Symbols and abbreviations am: tensile strength (MPa) ae: yield strength in (MPa). ar: failure strength in (MPa). A: elongations in Z: restriction in
HRV (30): Vickers hardness in (N/mm2). s: Nominal speed in (S-1). Y: Austenitic. a: Ferritic.
EI: Embrittlement indice in (%).
A0: Elongations specimen not charged, (Reference not charged (air). Ah: Elongations specimen charged in hydrogen. (Specimen charged).
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o w
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£ https://ifp.hal.science/hal-02475510 [Accessed: 20 March 2024].
"<5 >
O
x
Comportamiento mecánico del acero inoxidable austenítico cargado
C\l
° en la solución acuosa de H2SO4 durante ensayos de tracción
c¿ h
uj Amar Abboubac, autor de correspondencia, Ahmed Abourab,
Khaled Benmahdiad, Mohamed Sadounad,
O Mokhtar Belkacemac, Djameleddine Semsouma
Universidad Mustapha Stambouli, Facultad de Ciencias y Tecnología,
< Departamento de Ingeniería Mecánica, Mascara, República Argelina Democrática y Popular
q b Universidad Ahmed Zabana, Facultad de Ciencias y Tecnología,
w Departamento de Ingeniería Mecánica,
Relizane, República Argelina Democrática y Popular
R
< c Departamento de Ingeniería Mecánica d Departamento de Ingeniería Civil
Laboratorio para el Estudio de Estructuras y Mecánica de Materiales
CAMPO: materiales w TIPO DE ARTÍCULO: artículo científico original
L
o Resumen:
>0 Introducción/objetivo: Los aceros inoxidables tienen una excelente
resistencia a la corrosión y adecuadas propiedades mecánicas. Sin lü embargo, su uso en ambientes agresivamente hidrogenados en la industria
energética provoca una pérdida de ductilidad. Este trabajo estudió el efecto del hidrógeno sobre el comportamiento mecánico del acero inoxidable austenítico DINX15CrNiSi25.21/AISI310 cargado en una solución acuosa ffc de ácido puramente sulfúrico H2SO4 a 1N a temperatura ambiente durante
ensayos de tracción.
Métodos: Se aplican técnicas de caracterización experimental a probetas de tracción fabricadas mediante mecanizado estandarizado que se sometieron a una serie de tratamientos térmicos que van desde templado a 1050°C durante 35 minutos hasta revenido a 680°C durante 30 minutos. Esto va acompañado de una sucesión de inmersiones de estas muestras mediante ciclos de enfriamiento criogénico a -196°C durante una duración de 1 hora. El hidrógeno se cargó electrolíticamente en una celda de vidrio Pyrex durante varios tiempos de carga, que oscilaron entre 1h00 y 15h00, con un paso de 2h00.
Resultados: Los resultados mostraron una reducción en las propiedades mecánicas y la plasticidad. El método electroquímico confirmó la sensibilidad del material a la fragilización por hidrógeno, calculando el
a
criterio de fragiiización EI (%). Este método indica un rápido aumento de los valores en función de los tiempos de carga de hidrógeno, con un valor máximo del 41,60%.
Conclusión: El estudio destaca el impacto negativo del hidrógeno en las propiedades mecánicas del acero inoxidable AISI310, enfatizando la necesidad de reducir la exposición al hidrógeno en las aplicaciones de acero.
Palabras claves: acero inoxidable austenítico, tratamientos térmicos, precarga de hidrógeno, propiedades mecánicas, fragilización por hidrógeno (HE), caras.
Механическое поведение аустенитной нержавеющей стали, погруженной О в водный раствор H2SO4, при испытании на растяжение
Амар Аббоубав, корреспондент, Ахмед Абаураб, Халед Бенмахдиаг, Мухаммед Садунаг, Мйхтар Белкацемав, Джамелиддин Семсумав а Университет Мустафы Стамбули, факультет науки и технологии,
г. Маскара, Алжирская Народная Демократическая Республика б Университет Ахмеда Забаны, факультет науки и технологии, кафедра машиностроения,
Релизан, Алжирская Народная Демократическая Республика в кафедра машиностроения г отделение гражданского строительства, Лаборатория исследований структур и механики материалов
РУБРИКА ГРНТИ: 81.09.00 Материаловедение ВИД СТАТЬИ: оригинальная научная статья
Резюме:
Введение/цель: Нержавеющие стали обладают превосходной коррозионной стойкостью и соответствующими механическими свойствами. Однако их использование в агрессивно гидрированных средах в энергетической промышленности приводит к потере пластичности. В данной статье изучалось влияние водорода на механические свойства аустенитной нержавеющей стали DINX15CrNiSi25.21/AISI310, погруженной в водный раствор чистой серной кислоты H2SO4 при 1N при комнатной температуре во время испытания на растяжение. Методы: Экспериментальные методы определения характеристик применялись на стандартных образцах в испытании на растяжение. Образцы, изготовленные механической обработкой, подвергались ряду термообработок, начиная от закалки при температуре 1050°C в течение 35 минут и заканчивая отпуском при температуре 680°C в течение 30
см
о
^ минут. Испытание сопровождалось последовательным
| погружением образцов по циклам в криогенной закалки при
м температуре-196°С продолжительностью 60 минут. Получение
водорода производилось электролизом в емкости из термостойкого стекла в течение различного времени загрузки,
> варьирующегося от одного до пятнадцати часов с двухчасовым интервалом.
о
™ Результаты: Результаты показали снижение механических
2] свойств и пластичности. Электрохимический метод
Е подтвердил чувствительность материала к водородному
о охрупчиванию, рассчитав критерий охрупчивания Е1 (%). Данный
^ метод показывает быстрый рост значений в зависимости от
< времени загрузки водорода с максимальным значением 41,60%.
Вывод: В исследовании выявлено негативное влияние водорода на о механические свойства нержавеющей стали А!8!310, что
ш подчеркивает необходимость снижения воздействия водорода при
> производстве стали.
к Ключевые слова: аустенитная нержавеющая сталь,
термообработка, предварительная загрузка водорода, механические свойства, водородное охрупчивание (НЕ), поперечные сечения в месте повреждения.
Механичко понаша^е аустенитног нер^у^ег челика изложеног воденом раствору ЬЪБОд при испитива^у затеза^ем
ю <
о
Амар Абабав, аутор за преписку, Ахмед Абаура6, х Халед Бенмахдиаг, Мухамад Садуна
ш Моктар Белкацемав, Цамелидин Семсумав
а Универзитет „Мустафа Стамболи", Факултет науке и технолог^е, Маскара, Народна Демократска Република Алжир
6 Универзитет „Ахмед Забана", Факултет науке и технологов, Одсек за машинство,
Релизан, Народна Демократска Република Алжир в Одсек за машинство г Одсек за гра^евинарство,
Лаборатор^а за проучава^е конструкцф и механике материала ОБЛАСТ: матери]али
КАТЕГОРИJА (ТИП) ЧЛАНКА: оригинални научни рад Сажетак:
Увод/циж Нер^уПи челици има}у одличну отпорност на корозщу и одговара}уПа механичка сво]ства. Ме^утим, ньихова употреба у агресивним хидрогенизованим срединама у индустрии енергетике доводи до губитка дуктилности. У овом раду проучава се ефекат
со
водоника на механичко понашаъе аустенитног нер^уПег челика DINX15CrNiSi25.21/AISI310, оптереПеног у воденом раствору чисте сумпорне киселине (H2SO4) при Ш на собно] температури током испитиваъа на затезаъе.
Методе: Експерименталне технике карактеризацце примеъене су на стандардизоване затезне епрувете добцене машинском обрадом и подвргнуте серии термичких обрада - од каьеъа на 1050°С током 35 минута до отпуштаъа на 680°С током 30 минута. То ¡е праПено низом потапаъа епрувета током циклуса криогеног каьеъа на -196°С у тра]аъу од 60 минута. Водоник ¡е оптереПен електролитички у стаклено] посуди од пирекса за различита времена оптереПеъа, од ]едног сата до 15 сати, с о кораком од 2 сата.
Резултати: Резултати су показали редукована механичка сво]ства и пластичност. Електрохемцски метод ¡е потврдио осет^ивост материала на водоничну кртост, израчунаваъем критерцума кртости Е1 (%). Ова¡' метод указуе на брзи раст вредности зависно од времена оптереПеъа водоником, при чему ¡е максимална вредност 41,60%.
Закъучак: У раду се наглашава негативан утица] водоника на механичка сво]ства нер^а]уПег челика А^1310, при чему се истиче да уе при употреби челика потребно смаъити ньегову изложеност водонику.
К^учне речи: аустенитни нер^а]уПи челик, термичка обрада, претходно оптереПеъе водоником, механичка сво]ства, водонична кртост (НЕ), попречни пресеци на месту лома.
Paper received on: 21.03.2024.
Manuscript corrections submitted on: 16.11.2024.
Paper accepted for publishing on: 18.11.2024.
© 2024 The Authors. Published by Vojnotehnicki glasnik / Military Technical Courier (www.vtg.mod.gov.rs, BTr.M0.ynp.cp6). This article is an open access article distributed under the terms and conditions of the Creative Commons Attribution license (http://creativecommons.org/licenses/by/3.0/rs/).
