Hydrogen transport during a test and hydrogen segregation to twins, second phase particles and precipitation products prior to testing are shown to adversely effect the mechanical properties of metals. Hydrogen embrittlement processes in austenitic stainless steel, mild steel and aluminum occurred primarily by hydrogen induced weakening of the interfaces associated with specific metallographic features. In impact and slow bend tests of 21-6-9 and 304L stainless steels, the effect of hydrogen manifests itself in hydrogen induced faceted fracture along interfaces in the metal lattice. The extent of this weakening increases as the hydrogen content in the test sample is increased and during slow strain rate studies which promote hydrogen redistribution during the test. Disk rupture studies with 1015 and 1018 steels show that hydrogen segregation to the inclusion-matrix interface weakens the interface to such a degree that rapid fracture occurs. Studies with aluminum also indicate that hydrogen segregation to an interface degrades the mechanical properties. In age hardening experiments, hydrogen segregation caused an increase in the overaging kinetics in 2024 Al. This caused local softening of the aluminum and was probably due to the effect of hydrogen in promoting a loss of coherency at precipitate-matrix interfaces. The combined results of these tests support a decohesion type embrittlement mechanism, with the decohesion occurring at the interfaces. The results also suggest that any decohesion type mechanism must take into account the importance of hydrogen segregation and dislocation transport of hydrogen in the embrittlement process. / Master of Science

O aço SAE/AISI 52100 é utilizado para a fabricação de rolamentos como também na fabricação de outras peças e dispositivos como cames de eixo comando de válvulas. Um dos problemas desta liga é a necessidade de revenimentos em temperaturas muito baixas para obtenção de alta dureza e para evitar o fenômeno da fragilização da martensita revenida (FMR), em detrimento da tenacidade. Foi projetada uma nova liga Fe-C-Mn-Si-Cr (AISI/SAE 52100 modificado com 1,74% de Si e 0,96% de Mn) baseada na mesma ideia do aço 300M em relação ao SAE/AISI 4340. O efeito do Si na cinética de precipitação da cementita retarda a fragilização da martensita revenida (FMR), além de aumentar a dureza e mantê-la com valores relativamente altos mesmo quando do revenimento em temperaturas mais altas. A proposta do presente trabalho foi comprovar a resistência desta nova liga frente à FMR e demonstrar a resistência ao amolecimento perante o revenimento (curvas de revenimento). Com o intuito de estudar o efeito do Si na dureza do novo aço, foram elaboradas curvas de revenimento medindo-se essa propriedade em amostras do novo aço e do aço comercial após têmpera em temperaturas de austenitização na faixa de 825ºC e 960ºC, seguida por tratamento criogênico em nitrogênio líquido (-196ºC) durante doze horas e revenidas em temperaturas na faixa de 250ºC a 500ºC. Foram obtidas durezas acima de 60HRC, sendo que o aço modificado chegou a tingir 68HRC, no estado temperado. Foi estudada também a resistência ao amolecimento da nova liga e do aço comercial submetendo amostras em temperaturas constantes na faixa de 350ºC a 450ºC, variando-se o tempo na faixa de uma a dez horas. O aço modificado, após 10 horas em 450ºC, apresentou ainda, dureza de 58HRC. Para determinação das propriedades mecânicas desta nova liga foram realizados ensaios de tração em amostras temperadas e revenidas, comparativamente ao aço SAE/AISI 52100 comercial. Para a realização do estudo da FMR, foram comparados resultados dos ensaios de impacto para o aço SAE/AISI 52100 comercial (0,25%Si) e modificado (1,74%Si). O aço modificado não apresentou o fenômeno da FMR. Foram analisados aspectos microestruturais por meio de microscopia eletrônica de varredura (MEV) e difração de raios-x. / The SAE/AISI 52100 steel is used for bearing manufacturing and automotive parts like camshafts lobes. A problem with this alloy is the need for low tempering temperature in order to obtain high hardness and to avoid the tempered martensite embrittlement phenomena, compromising the toughness. Based on the same idea as 300M steel regarding SAE/AISI 4340 steel, a new Fe-C-Mn-Si-Cr bearing alloy (AISI 52100 steel, modified with 1.74% Si and 0.96%Mn) was developed. The effect of Si on the kinetics of cementite precipitation leads to a higher temperature of tempered martensite embrittlement (TME) occurrence and keep high hardness values even when the steel is submitted to a higher temperatures tempering or for long time. The purpose of this work was to confirm the new alloy tempered martensite embrittlement (TME) resistance and to verify its softening resistance (tempering curves). Intending to investigate the Si effect on new steel hardness, hardness measurements were performed on modified and commercial steels samples after 825ºC 960ºC austenitization, twelve hours -196ºC cryogenic treatment and 250ºC 500ºC tempering. It was obtained hardness values over 60HRC and the modified steel presented 68HRC as quenched. The new alloy and commercial alloy softening resistance was studied by hardness measurement on samples submitted to 350ºC 450ºC constant temperature tempering in periods of time from one to ten hours. The Si alloyed steel presented 58HRC after 10 hours at 450ºC. For the mechanical characterization of the new alloy, tensile tests were performed in quenched and tempered samples. In the tempered martensite embrittlement study, impact tests results for commercial SAE/AISI 52100 (0.25%Si) and modified (1.74%Si) were compared. The modified steel presented no tempered martensite embrittlement. Microstructural aspects were studied by scanning electron microscopy and x-ray diffraction analysis.

Die Anwendbarkeit des Master Curve-(MC-)Konzepts zur Charakterisierung des Zähigkeitszustandes bestrahlter Reaktordruck¬behälter-(RDB-)Stähle wurde an drei RDB-Stählen überprüft: IAEA-Referenzstahl 3JRQ57, 1JFL11 (vergleichbar mit 22NiMoCr3-7) sowie russischer WWER-440 Grundwerkstoff KAB-B. In Zugversuchen, Charpy-V-Tests, Risswiderstandskurven nach ASTM E1820 und Master Curve Tests zur Bestimmung der Referenztemperatur T0 nach ASTM E1921 wurden der unbestrahlte Ausgangszustand, je drei Bestrahlungszustände bis hin zu Neutronenfluenzen von 100∙10^18 n/cm² (E>1MeV) sowie bei 475°C/100h thermisch ausgeheilte Zustände untersucht. Mit zusätzlichen auf dem MC-Konzept basierenden Auswerteverfahren nach SINTAP, multimodalem MC-Ansatz (MML) sowie der Unified Curve erfolgte die Bewertung des Einflusses von Materialinhomogenitäten und möglicher MC-Formänderung bei hohen Fluenzen. Wie erwartet geht Neutronenbestrahlung mit Verfestigung und Duktilitätsabnahme einher, d.h. Härte, Festigkeitskennwerte, Charpy-V-Übergangstemperaturen T28J und T41J sowie T0 steigen mit der Neutronenfluenz, während die Bruchdehnung und Hochlagenzähigkeit abnehmen. Am bestrahlungsempfindlichsten reagiert der Stahl 3JRQ57, gefolgt von KAB-B und 1JFL11. Durch die Ausheilbehandlung von 475°C/100h erholen sich die Werkstoffkennwerte der Zugversuche, Charpy-V-Tests und MC-Versuche auf den jeweiligen unbestrahlten Ausgangszustand. Die technischen Ersatzkennwerte für duktile Rissinitiierung bleiben relativ unbeeinflusst von der Neutronenbestrahlung. Die MC nach ASTM E1921 beschreibt die Bruchzähigkeits-Temperaturverläufe für alle drei RDB-Stähle in allen Bestrahlungs- und Ausheilzuständen gut. Bei den niedrig und mittel bestrahlten Zuständen liegen meist mehr als 5% der KJc(1T)-Werte unterhalb der MC-Kurve für 5% Versagenswahrscheinlichkeit. Die MC beschreibt den hoch bestrahlte Zustand (ca. 100∙10^18 n/cm², E>1MeV) aller drei RDB-Stähle sehr gut, auch für Daten außerhalb des Gültigkeitsbereiches T0±50K, und auch für den bestrahlungsempfindlichen 3JRQ57 mit inhomogenem Gefüge. Die Unified Curve überbewertet den Einfluss der Neutronenbestrahlung auf die MC-Kurvenform. Eine mögliche Formänderung der MC durch Neutronenbestrahlung konnte bei keinem der drei untersuchten RDB-Stähle nachgewiesen werden.

The imminent emergence of the hydrogen fuel industry has resulted in an urgent mandate for very specific material testing. Although storage of pressurized hydrogen gas is both practical and attainable, demands for increasing storage pressures (currently around 70 MPa) continue to present unexpected material compatibility issues. It is imperative that materials commonly used in gaseous hydrogen service are properly tested for hydrogen embrittlement resistance. To assess material behavior in a pressurized hydrogen environment, procedures were designed to test materials for susceptibility to hydrogen embrittlement. Of particular interest to the field of high-pressure hydrogen in the automotive industry, austenitic stainless steels SUS 316 and 316L were used to validate the test programs. Tests were first performed in 25 MPa helium and hydrogen at room temperature and at -40°C. Tests in a 25 MPa hydrogen atmosphere caused embrittlement in SUS 316, but not in 316L. This indicated that alloys with higher stacking fault energies (316L) are more resistant to hydrogen embrittlement. Decreasing the test temperature caused slight embrittlement in 316L and significantly enhanced it in 316. Alternatively, a second set of specimens was immersed in 70 MPa hydrogen at 100°C until reaching a uniform concentration of absorbed hydrogen. Specimens were then loaded in tension to failure to determine if a bulk saturation of hydrogen provided a similar embrittling effect. Neither material succumbed to the effects of gaseous pre-charging, indicating that the embrittling mechanism requires a constant supply of hydrogen at the material surface rather than having bulk concentration of dissolved hydrogen. Permeation tests were also performed to ensure that hydrogen penetrated the samples and to develop material specific permeation constants. To pave the way for future work, prototype equipment was constructed allowing tensile or fatigue tests to be performed at much higher hydrogen pressures. To determine the effect of pressure on hydrogen embrittlement, additional tests can be performed in hydrogen pressures up to 85 MPa hydrogen. The equipment will also allow for cyclic loading of notched tensile or compact tension specimens for fatigue studies.

The imminent emergence of the hydrogen fuel industry has resulted in an urgent mandate for very specific material testing. Although storage of pressurized hydrogen gas is both practical and attainable, demands for increasing storage pressures (currently around 70 MPa) continue to present unexpected material compatibility issues. It is imperative that materials commonly used in gaseous hydrogen service are properly tested for hydrogen embrittlement resistance. To assess material behavior in a pressurized hydrogen environment, procedures were designed to test materials for susceptibility to hydrogen embrittlement. Of particular interest to the field of high-pressure hydrogen in the automotive industry, austenitic stainless steels SUS 316 and 316L were used to validate the test programs. Tests were first performed in 25 MPa helium and hydrogen at room temperature and at -40°C. Tests in a 25 MPa hydrogen atmosphere caused embrittlement in SUS 316, but not in 316L. This indicated that alloys with higher stacking fault energies (316L) are more resistant to hydrogen embrittlement. Decreasing the test temperature caused slight embrittlement in 316L and significantly enhanced it in 316. Alternatively, a second set of specimens was immersed in 70 MPa hydrogen at 100°C until reaching a uniform concentration of absorbed hydrogen. Specimens were then loaded in tension to failure to determine if a bulk saturation of hydrogen provided a similar embrittling effect. Neither material succumbed to the effects of gaseous pre-charging, indicating that the embrittling mechanism requires a constant supply of hydrogen at the material surface rather than having bulk concentration of dissolved hydrogen. Permeation tests were also performed to ensure that hydrogen penetrated the samples and to develop material specific permeation constants. To pave the way for future work, prototype equipment was constructed allowing tensile or fatigue tests to be performed at much higher hydrogen pressures. To determine the effect of pressure on hydrogen embrittlement, additional tests can be performed in hydrogen pressures up to 85 MPa hydrogen. The equipment will also allow for cyclic loading of notched tensile or compact tension specimens for fatigue studies.

Hydrogen embrittlement (HE), which results in an unpredictable failure of metals, has been a major limitation in the design of critical components for a wide range of engineering applications, given the near-ubiquitous presence of hydrogen in their service environments. However, the exact mechanisms that underpin HE failure remain poorly understood. It is known that hydrogen, when free to diffuse in these materials, can tend to concentrate at a crack tip front. In turn, this facilitates crack propagation. Hence one of the proposed strategies for mitigating HE is to limit the content of freely diffusing hydrogen within the metal atomic lattice via the introduction of microstructural hydrogen traps. Further, it is empirically known that the introduction of finely-dispersed distribution of nano-sized carbide hydrogen traps in ferritic steel matrix can improve resilience to HE. This resilience has been attributed to the effective hydrogen trapping of the carbides. However, conclusive atomic-scale experimental evidence is still lacking as to the manner by which these features can impede the movement of the hydrogen. This lack of insight limits the further progress for the optimisation of the microstructural design of this type of HE-resistant steel. In order to further understand the hydrogen trapping phenomenon of the nano-sized carbide in steel, an appropriate characterisation method is required. Atom probe tomography (APT) has been known for its powerful combination of high 3D spatial and chemical resolution for the analysis of very fine precipitates. Furthermore, previous studies have shown that the application of isotopic hydrogen (²H) loading techniques, combined with APT, facilitates the hydrogen signal associated to fine carbides to be unambiguously identified. However, the considerable experimental requirements as utilised by these previous studies, particularly the instrumental capability necessary for retention of the trapped hydrogen in the needle-shaped APT specimen, limits the study being reproduced or extended. In this APT study, a model ferritic steel with finely dispersed V-Mo-Nb carbides of 10-20 nm is investigated. Initially, existing specialised instrumentation formed the basis of a cryogenic specimen chain under vacuum, so as to retain loaded hydrogen after an electrolytic charging treatment for APT analysis. This work confirms the importance of cryogenic treatment for the retention of trapped hydrogen in APT specimen. The quality of the obtained experimental data allows a quantitative analysis on the hydrogen trapping mechanism. Thus, it is conclusively determined that interior of the carbides studied in this steel acts as the hydrogen trapping site as opposed to the carbide/matrix interface as commonly expected. This result supports the theoretical investigations proposing that the hydrogen trapping within the carbide interior is enabled by a network of carbon vacancies. Based on the established importance of the specimen cold chain in these APT experiments, this work then successfully develops a simplified approach to cryo-transfer which requires no instrumental modification. In this approach there is no requirement for the charged specimen to be transferred under vacuum conditions. The issue of environmental-induced ice contamination on the cryogenic sample surface in air transfer is resolved by its sublimation in APT vacuum chamber. Furthermore, the temperature of the transferred sample is able to be determined independently by both monitoring changes to vacuum pressure in the buffer chamber and also the thermal response of the APT sample stage in the analysis chamber. This simplified approach has the potential to open up a range of hydrogen trapping studies to any commercial atom probe instrument. Finally, as an example of the use of this simplified cryo-transfer technique, targeted studies for determining the source of hydrogen adsorption during electropolishing and electrolytic loading process are demonstrated. This research provides a critical verification of hydrogen trapping mechanism of fine carbides as well as an achievable experimental protocol for the observation of the trapping of individual hydrogen atoms in alloy microstructures. The methods developed here have the potential to underpin a wide range of possible experiments which address the HE problem, particularly for the design of new mitigation strategies to prevent this critical issue.

O aço SAE/AISI 52100 é utilizado para a fabricação de rolamentos como também na fabricação de outras peças e dispositivos como cames de eixo comando de válvulas. Um dos problemas desta liga é a necessidade de revenimentos em temperaturas muito baixas para obtenção de alta dureza e para evitar o fenômeno da fragilização da martensita revenida (FMR), em detrimento da tenacidade. Foi projetada uma nova liga Fe-C-Mn-Si-Cr (AISI/SAE 52100 modificado com 1,74% de Si e 0,96% de Mn) baseada na mesma ideia do aço 300M em relação ao SAE/AISI 4340. O efeito do Si na cinética de precipitação da cementita retarda a fragilização da martensita revenida (FMR), além de aumentar a dureza e mantê-la com valores relativamente altos mesmo quando do revenimento em temperaturas mais altas. A proposta do presente trabalho foi comprovar a resistência desta nova liga frente à FMR e demonstrar a resistência ao amolecimento perante o revenimento (curvas de revenimento). Com o intuito de estudar o efeito do Si na dureza do novo aço, foram elaboradas curvas de revenimento medindo-se essa propriedade em amostras do novo aço e do aço comercial após têmpera em temperaturas de austenitização na faixa de 825ºC e 960ºC, seguida por tratamento criogênico em nitrogênio líquido (-196ºC) durante doze horas e revenidas em temperaturas na faixa de 250ºC a 500ºC. Foram obtidas durezas acima de 60HRC, sendo que o aço modificado chegou a tingir 68HRC, no estado temperado. Foi estudada também a resistência ao amolecimento da nova liga e do aço comercial submetendo amostras em temperaturas constantes na faixa de 350ºC a 450ºC, variando-se o tempo na faixa de uma a dez horas. O aço modificado, após 10 horas em 450ºC, apresentou ainda, dureza de 58HRC. Para determinação das propriedades mecânicas desta nova liga foram realizados ensaios de tração em amostras temperadas e revenidas, comparativamente ao aço SAE/AISI 52100 comercial. Para a realização do estudo da FMR, foram comparados resultados dos ensaios de impacto para o aço SAE/AISI 52100 comercial (0,25%Si) e modificado (1,74%Si). O aço modificado não apresentou o fenômeno da FMR. Foram analisados aspectos microestruturais por meio de microscopia eletrônica de varredura (MEV) e difração de raios-x. / The SAE/AISI 52100 steel is used for bearing manufacturing and automotive parts like camshafts lobes. A problem with this alloy is the need for low tempering temperature in order to obtain high hardness and to avoid the tempered martensite embrittlement phenomena, compromising the toughness. Based on the same idea as 300M steel regarding SAE/AISI 4340 steel, a new Fe-C-Mn-Si-Cr bearing alloy (AISI 52100 steel, modified with 1.74% Si and 0.96%Mn) was developed. The effect of Si on the kinetics of cementite precipitation leads to a higher temperature of tempered martensite embrittlement (TME) occurrence and keep high hardness values even when the steel is submitted to a higher temperatures tempering or for long time. The purpose of this work was to confirm the new alloy tempered martensite embrittlement (TME) resistance and to verify its softening resistance (tempering curves). Intending to investigate the Si effect on new steel hardness, hardness measurements were performed on modified and commercial steels samples after 825ºC 960ºC austenitization, twelve hours -196ºC cryogenic treatment and 250ºC 500ºC tempering. It was obtained hardness values over 60HRC and the modified steel presented 68HRC as quenched. The new alloy and commercial alloy softening resistance was studied by hardness measurement on samples submitted to 350ºC 450ºC constant temperature tempering in periods of time from one to ten hours. The Si alloyed steel presented 58HRC after 10 hours at 450ºC. For the mechanical characterization of the new alloy, tensile tests were performed in quenched and tempered samples. In the tempered martensite embrittlement study, impact tests results for commercial SAE/AISI 52100 (0.25%Si) and modified (1.74%Si) were compared. The modified steel presented no tempered martensite embrittlement. Microstructural aspects were studied by scanning electron microscopy and x-ray diffraction analysis.

Masters of Science / Nampak packages millions of cans a year and a very small percentage of these cans fail due to many reasons. One of the main reasons that cause 2- piece food cans to fail is split flanges. Split Flanges arises due to a number of reasons which will be discussed in detail.The focus of this thesis was based on the causes of split flanges in 2-piece food cans. A study on manufacturing the steel and can making together with packaging fish in these cans was conducted. Another study on the reasons for split flanges occurring in 2 piece cans was conducted done as well.The purpose of the investigation was to check if hydrogen embrittlement could be the cause for split bodies forming in 2 piece food cans. 2 piece cans are drawn and wall ironed from tinplate; the cans were made up of a top and a shaped body. It was this shaped body that went through a considerable amount of stress during manufacture especially at the top of the can, which gave an explanation to why the cans split at the curved area near the flange of the can.According to previous studies done at Nampak R&D more complaints about split bodies were coming from the Fish canneries on the West Coast than the Vegetable canneries. These canneries used the exact same cans to package their product. The difference between the processes at these canneries was the exhaust boxes at the fish canneries. The exhaust box is a long tunnel filled with steam used to precook the fish; the vegetables are not precooked in exhaust boxes. Non metallic inclusions (NMI) was one of the main reason for these split flanges to occur and a reason of particular interest in this research.NMI’s were distributed throughout the steel of the cans and since the same cans were used for the fish and vegetable canneries, they should be failing at the same rate. Yet only complaints came from the fish canneries. So the primary focus of the research was to check if the additional steam process contributed to the formation of split bodies / flanges. We proposed to investigate if hydrogen atoms collect at grain boundaries, vacancies and non metallic inclusions and also to check if the steam accelerated embrittlement. Hydrogen is believed to penetrate right into the bare steel of the cans that were exposed to steam.Hydrogen atoms are being investigated because of their small size, their ability to diffuse through a metal lattice and form hydrogen molecules within the intermetallic vacancies of the metal. The molecules of hydrogen, once formed within the internal structure of the metal, remain trapped because of their larger size and can generate a significant pressure that can contribute to the formation of split bodies. [1] The first step to prove whether H-embrittlement was present in the cans was to check if hydrogen was present. A spectroscopic method namely, elastic recoil detection analysis (ERDA) was used to check if H could be detected using the Elastic Recoil Detection Analysis technique. Several experiments were designed to make sure the technique was suitable for the detection of H. Even though it is known that all metals are susceptible to corrosion and Hembrittlement, the tinplate metals had to be checked in an environment similar to the exhaust box (suspected area causing hydrogen embrittlement) in the factories.Further characterization was done using X-Ray Diffraction to measure the residual stress and relate it to the effects of H-embrittlement. If the H had penetrated into the metal it would cause some distortion in the atomic distances between the atomic planes in Fe atoms and can be measured using XRD.Another effect of hydrogen embrittlement is to reduce the strength in the metal. Tensile tests were performed to measure the strengths of the metal.

The imminent emergence of the hydrogen fuel industry has resulted in an urgent mandate for very specific material testing. Although storage of pressurized hydrogen gas is both practical and attainable, demands for increasing storage pressures (currently around 70 MPa) continue to present unexpected material compatibility issues. It is imperative that materials commonly used in gaseous hydrogen service are properly tested for hydrogen embrittlement resistance. To assess material behavior in a pressurized hydrogen environment, procedures were designed to test materials for susceptibility to hydrogen embrittlement. Of particular interest to the field of high-pressure hydrogen in the automotive industry, austenitic stainless steels SUS 316 and 316L were used to validate the test programs. Tests were first performed in 25 MPa helium and hydrogen at room temperature and at -40°C. Tests in a 25 MPa hydrogen atmosphere caused embrittlement in SUS 316, but not in 316L. This indicated that alloys with higher stacking fault energies (316L) are more resistant to hydrogen embrittlement. Decreasing the test temperature caused slight embrittlement in 316L and significantly enhanced it in 316. Alternatively, a second set of specimens was immersed in 70 MPa hydrogen at 100°C until reaching a uniform concentration of absorbed hydrogen. Specimens were then loaded in tension to failure to determine if a bulk saturation of hydrogen provided a similar embrittling effect. Neither material succumbed to the effects of gaseous pre-charging, indicating that the embrittling mechanism requires a constant supply of hydrogen at the material surface rather than having bulk concentration of dissolved hydrogen. Permeation tests were also performed to ensure that hydrogen penetrated the samples and to develop material specific permeation constants. To pave the way for future work, prototype equipment was constructed allowing tensile or fatigue tests to be performed at much higher hydrogen pressures. To determine the effect of pressure on hydrogen embrittlement, additional tests can be performed in hydrogen pressures up to 85 MPa hydrogen. The equipment will also allow for cyclic loading of notched tensile or compact tension specimens for fatigue studies. / Applied Science, Faculty of / Materials Engineering, Department of / Graduate

Die Anwendbarkeit des Master Curve-(MC-)Konzepts zur Charakterisierung des Zähigkeitszustandes bestrahlter Reaktordruck¬behälter-(RDB-)Stähle wurde an drei RDB-Stählen überprüft: IAEA-Referenzstahl 3JRQ57, 1JFL11 (vergleichbar mit 22NiMoCr3-7) sowie russischer WWER-440 Grundwerkstoff KAB-B. In Zugversuchen, Charpy-V-Tests, Risswiderstandskurven nach ASTM E1820 und Master Curve Tests zur Bestimmung der Referenztemperatur T0 nach ASTM E1921 wurden der unbestrahlte Ausgangszustand, je drei Bestrahlungszustände bis hin zu Neutronenfluenzen von 100∙10^18 n/cm² (E>1MeV) sowie bei 475°C/100h thermisch ausgeheilte Zustände untersucht. Mit zusätzlichen auf dem MC-Konzept basierenden Auswerteverfahren nach SINTAP, multimodalem MC-Ansatz (MML) sowie der Unified Curve erfolgte die Bewertung des Einflusses von Materialinhomogenitäten und möglicher MC-Formänderung bei hohen Fluenzen. Wie erwartet geht Neutronenbestrahlung mit Verfestigung und Duktilitätsabnahme einher, d.h. Härte, Festigkeitskennwerte, Charpy-V-Übergangstemperaturen T28J und T41J sowie T0 steigen mit der Neutronenfluenz, während die Bruchdehnung und Hochlagenzähigkeit abnehmen. Am bestrahlungsempfindlichsten reagiert der Stahl 3JRQ57, gefolgt von KAB-B und 1JFL11. Durch die Ausheilbehandlung von 475°C/100h erholen sich die Werkstoffkennwerte der Zugversuche, Charpy-V-Tests und MC-Versuche auf den jeweiligen unbestrahlten Ausgangszustand. Die technischen Ersatzkennwerte für duktile Rissinitiierung bleiben relativ unbeeinflusst von der Neutronenbestrahlung. Die MC nach ASTM E1921 beschreibt die Bruchzähigkeits-Temperaturverläufe für alle drei RDB-Stähle in allen Bestrahlungs- und Ausheilzuständen gut. Bei den niedrig und mittel bestrahlten Zuständen liegen meist mehr als 5% der KJc(1T)-Werte unterhalb der MC-Kurve für 5% Versagenswahrscheinlichkeit. Die MC beschreibt den hoch bestrahlte Zustand (ca. 100∙10^18 n/cm², E>1MeV) aller drei RDB-Stähle sehr gut, auch für Daten außerhalb des Gültigkeitsbereiches T0±50K, und auch für den bestrahlungsempfindlichen 3JRQ57 mit inhomogenem Gefüge. Die Unified Curve überbewertet den Einfluss der Neutronenbestrahlung auf die MC-Kurvenform. Eine mögliche Formänderung der MC durch Neutronenbestrahlung konnte bei keinem der drei untersuchten RDB-Stähle nachgewiesen werden.