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Tetsu-to-Hagané Vol. 110 (2024), No. 16

ISIJ International
belloff

Grid List Abstracts
ONLINE ISSN: 1883-2954
PRINT ISSN: 0021-1575
Publisher: The Iron and Steel Institute of Japan

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  1. Vol. 110 (2024)

    1. No.16
    2. No.15
    3. No.14
    4. No.13
    5. No.12
    6. No.11
    7. No.10
    8. No.9
    9. No.8
    10. No.7
    11. No.6
    12. No.5
    13. No.4
    14. No.3
    15. No.2
    16. No.1

  2. Vol. 109 (2023)

    1. No.12
    2. No.11
    3. No.10
    4. No.9
    5. No.8
    6. No.7
    7. No.6
    8. No.5
    9. No.4
    10. No.3
    11. No.2
    12. No.1

  3. Vol. 108 (2022)

    1. No.12
    2. No.11
    3. No.10
    4. No.9
    5. No.8
    6. No.7
    7. No.6
    8. No.5
    9. No.4
    10. No.3
    11. No.2
    12. No.1

  4. Vol. 107 (2021)

    1. No.12
    2. No.11
    3. No.10
    4. No.9
    5. No.8
    6. No.7
    7. No.6
    8. No.5
    9. No.4
    10. No.3
    11. No.2
    12. No.1

  5. Vol. 106 (2020)

    1. No.12
    2. No.11
    3. No.10
    4. No.9
    5. No.8
    6. No.7
    7. No.6
    8. No.5
    9. No.4
    10. No.3
    11. No.2
    12. No.1

  6. Vol. 105 (2019)

    1. No.12
    2. No.11
    3. No.10
    4. No.9
    5. No.8
    6. No.7
    7. No.6
    8. No.5
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    10. No.3
    11. No.2
    12. No.1

  7. Vol. 104 (2018)

    1. No.12
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    3. No.10
    4. No.9
    5. No.8
    6. No.7
    7. No.6
    8. No.5
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    10. No.3
    11. No.2
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  8. Vol. 103 (2017)

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    4. No.9
    5. No.8
    6. No.7
    7. No.6
    8. No.5
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    11. No.2
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  9. Vol. 102 (2016)

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    5. No.8
    6. No.7
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    8. No.5
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  10. Vol. 101 (2015)

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    5. No.8
    6. No.7
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  11. Vol. 100 (2014)

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    5. No.8
    6. No.7
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  12. Vol. 99 (2013)

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    5. No.8
    6. No.7
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    8. No.5
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    10. No.3
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  13. Vol. 98 (2012)

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    4. No.9
    5. No.8
    6. No.7
    7. No.6
    8. No.5
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    10. No.3
    11. No.2
    12. No.1

  14. Vol. 97 (2011)

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    5. No.8
    6. No.7
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  15. Vol. 96 (2010)

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    5. No.8
    6. No.7
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  16. Vol. 95 (2009)

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    5. No.8
    6. No.7
    7. No.6
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  17. Vol. 94 (2008)

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    3. No.10
    4. No.9
    5. No.8
    6. No.7
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    8. No.5
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  18. Vol. 93 (2007)

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    3. No.10
    4. No.9
    5. No.8
    6. No.7
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  19. Vol. 92 (2006)

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    5. No.8
    6. No.7
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  20. Vol. 91 (2005)

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    6. No.7
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  21. Vol. 90 (2004)

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    6. No.7
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  22. Vol. 89 (2003)

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    6. No.7
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  23. Vol. 88 (2002)

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    4. No.9
    5. No.8
    6. No.7
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  24. Vol. 87 (2001)

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    2. No.11
    3. No.10
    4. No.9
    5. No.8
    6. No.7
    7. No.6
    8. No.5
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  25. Vol. 86 (2000)

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    3. No.10
    4. No.9
    5. No.8
    6. No.7
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  26. Vol. 85 (1999)

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    3. No.10
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    5. No.8
    6. No.7
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  27. Vol. 84 (1998)

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    2. No.11
    3. No.10
    4. No.9
    5. No.8
    6. No.7
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    10. No.3
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    12. No.1

  28. Vol. 83 (1997)

    1. No.12
    2. No.11
    3. No.10
    4. No.9
    5. No.8
    6. No.7
    7. No.6
    8. No.5
    9. No.4
    10. No.3
    11. No.2
    12. No.1

  29. Vol. 82 (1996)

    1. No.12
    2. No.11
    3. No.10
    4. No.9
    5. No.8
    6. No.7
    7. No.6
    8. No.5
    9. No.4
    10. No.3
    11. No.2
    12. No.1

  30. Vol. 81 (1995)

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    3. No.10
    4. No.9
    5. No.8
    6. No.7
    7. No.6
    8. No.5
    9. No.4
    10. No.3
    11. No.2
    12. No.1

  31. Vol. 80 (1994)

    1. No.12
    2. No.11
    3. No.10
    4. No.9
    5. No.8
    6. No.7
    7. No.6
    8. No.5
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    10. No.3
    11. No.2
    12. No.1

  32. Vol. 79 (1993)

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    2. No.11
    3. No.10
    4. No.9
    5. No.8
    6. No.7
    7. No.6
    8. No.5
    9. No.4
    10. No.3
    11. No.2
    12. No.1

  33. Vol. 78 (1992)

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    3. No.10
    4. No.9
    5. No.8
    6. No.7
    7. No.6
    8. No.5
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    10. No.3
    11. No.2
    12. No.1

  34. Vol. 77 (1991)

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    3. No.10
    4. No.9
    5. No.8
    6. No.7
    7. No.6
    8. No.5
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    11. No.2
    12. No.1

  35. Vol. 76 (1990)

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    3. No.10
    4. No.9
    5. No.8
    6. No.7
    7. No.6
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    10. No.3
    11. No.2
    12. No.1

  36. Vol. 75 (1989)

    1. No.12
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    3. No.10
    4. No.9
    5. No.8
    6. No.7
    7. No.6
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    10. No.3
    11. No.2
    12. No.1

  37. Vol. 74 (1988)

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    3. No.10
    4. No.9
    5. No.8
    6. No.7
    7. No.6
    8. No.5
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    10. No.3
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    12. No.1

  38. Vol. 73 (1987)

    1. No.16
    2. No.15
    3. No.14
    4. No.13
    5. No.12
    6. No.11
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    8. No.9
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    11. No.6
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    15. No.2
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  39. Vol. 72 (1986)

    1. No.16
    2. No.15
    3. No.14
    4. No.13
    5. No.12
    6. No.11
    7. No.10
    8. No.9
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    10. No.7
    11. No.6
    12. No.5
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  40. Vol. 71 (1985)

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    2. No.15
    3. No.14
    4. No.13
    5. No.12
    6. No.11
    7. No.10
    8. No.9
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    10. No.7
    11. No.6
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  41. Vol. 70 (1984)

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    3. No.14
    4. No.13
    5. No.12
    6. No.11
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    8. No.9
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  42. Vol. 69 (1983)

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    3. No.14
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    5. No.12
    6. No.11
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  43. Vol. 68 (1982)

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  44. Vol. 67 (1981)

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    3. No.14
    4. No.13
    5. No.12
    6. No.11
    7. No.10
    8. No.9
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    10. No.7
    11. No.6
    12. No.5
    13. No.4
    14. No.3
    15. No.2
    16. No.1

  45. Vol. 66 (1980)

    1. No.14
    2. No.13
    3. No.12
    4. No.11
    5. No.10
    6. No.9
    7. No.8
    8. No.7
    9. No.6
    10. No.5
    11. No.4
    12. No.3
    13. No.2
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  46. Vol. 65 (1979)

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    3. No.12
    4. No.11
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    6. No.9
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  47. Vol. 64 (1978)

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    3. No.12
    4. No.11
    5. No.10
    6. No.9
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    8. No.7
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    11. No.4
    12. No.3
    13. No.2
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  48. Vol. 63 (1977)

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    3. No.12
    4. No.11
    5. No.10
    6. No.9
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    8. No.7
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    10. No.5
    11. No.4
    12. No.3
    13. No.2
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  49. Vol. 62 (1976)

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    7. No.8
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  50. Vol. 61 (1975)

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    3. No.13
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    5. No.11
    6. No.10
    7. No.9
    8. No.8
    9. No.7
    10. No.6
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    12. No.4
    13. No.3
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  51. Vol. 60 (1974)

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    6. No.9
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  52. Vol. 59 (1973)

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  53. Vol. 58 (1972)

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  54. Vol. 57 (1971)

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  55. Vol. 56 (1970)

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  56. Vol. 55 (1969)

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  57. Vol. 54 (1968)

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  58. Vol. 53 (1967)

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  59. Vol. 52 (1966)

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  60. Vol. 51 (1965)

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  61. Vol. 50 (1964)

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  62. Vol. 49 (1963)

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  63. Vol. 48 (1962)

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  64. Vol. 47 (1961)

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  65. Vol. 46 (1960)

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  66. Vol. 45 (1959)

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  67. Vol. 44 (1958)

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  68. Vol. 43 (1957)

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  69. Vol. 42 (1956)

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  70. Vol. 41 (1955)

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Tetsu-to-Hagané Vol. 110 (2024), No. 16

Effect of Initial Microstructures on Grain Refinement by Burnishing

Yoshinori Amano, Takahisa Suzuki, Kaori Kawano

pp. 1251-1263

DOI:

10.2355/tetsutohagane.TETSU-2024-086

Abstract

The development of ultrafine grained microstructures under severe plastic deformation by burnishing process was investigated using spherical cementite-ferrite (SA) steel and pearlite (P) steel of AISI 52100. Microstructures were analyzed using FE-SEM, FE-TEM and EBSD observations. In the SA steel, equiaxed ultrafine ferrite grains were formed at the burnished surface where the equivalent strain was about 3.9. These ultrafine grains were formed by continuous dynamic recrystallization because they consisted of high angle grain boundaries. On the other hand, in the P steel, the initial lamellar structure was maintained even at the equivalent strain about 4.3, and ferrite grains with a large aspect ratio were formed. These ferrite grains were considered to be non-recrystallized grains because the KAM value within these grains was high. In addition, many dislocation contrasts in the same direction were observed within a ferrite grain by FE-TEM observation. These results suggested that active dislocation slip system in these ferrite grains is limited by lamellar structure. As the strain increased by repeated burnishing process, these ferrite grains of P steel became coarse and the KAM value within these grains decreased. In addition, several dislocation contrasts in multiple directions were observed within a ferrite grain. It can be concluded that the limitation of active dislocation slip system in these ferrite grains were relaxed, and dynamic recovery was occurred in these ferrite grains.

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Effect of Initial Microstructures on Grain Refinement by Burnishing

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Influence of Silicon Contents on the Microstructure and Tensile Properties of Quenching and Partitioning (Q&P) Processed Low Carbon Steel

Chang Jae Yu, Chang-Hyo Seo, Young-Roc Im, Dong-Woo Suh

pp. 1264-1274

DOI:

10.2355/tetsutohagane.TETSU-2024-088

Abstract

The microstructure and corresponding tensile properties were examined in quenching and partitioning (Q&P) processed low carbon steels, depending on the silicon content ranging from 0.1–2.0 wt.%. The silicon content and process temperature generated a highly interactive influence on the evolution of final microstructure, including the fraction of constituent phases and their characteristics such as solute carbon content in each phase. The yield strength was nearly unchanged or slightly decreased even with the silicon addition for a given Q&P condition. The change of yield strength showed a reasonable correlation with the loss of solute carbon in martensite or bainite caused by the carbide precipitation and the carbon partitioning into austenite, which depended on the silicon content. High partitioning temperature enhanced the yield strength for a given silicon content and quenching condition, because of the tempering effect on the martensite matrix. Although the fraction and stability of retained austenite were still critical for improving ductility, the intrinsic properties of the martensite matrix, such as the occurrence of tempered martensite embrittlement, governed the ductility of Q&P steels in situations where the role of retained austenite was limited due to low fraction or poor mechanical stability.

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Influence of Silicon Contents on the Microstructure and Tensile Properties of Quenching and Partitioning (Q&P) Processed Low Carbon Steel

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Hydrogen Content Dependence of the Contribution of Dislocation-slip Stability and Carbide Precipitation Morphology to the Hydrogen Embrittlement Property of High-strength Martensitic Steels

Kei Saito, Kenichi Takai

pp. 1275-1287

DOI:

10.2355/tetsutohagane.TETSU-2024-091

Abstract

The contribution of dislocation-slip stability and carbide precipitation morphology to the hydrogen embrittlement (HE) property of tempered martensitic steels with low and high silicon contents (L-Si and H-Si) and oil-quenched martensitic steel (As-OQ), was evaluated by conducting slow strain rate tests. The order of dislocation-slip stability was the H-Si specimen > L-Si specimen > As-OQ specimen. The H-Si and As-OQ specimens had finely dispersed carbides inside prior austenite (γ) grains, whereas the L-Si specimen had coarsely dispersed carbides inside prior γ grains and on the boundaries. Notched specimens were charged with hydrogen in a range of low (0.19–0.31 ppm), medium (1.04–1.49 ppm), and high (2.17–2.33 ppm) hydrogen contents. The H-Si specimen had the highest HE property under the three hydrogen charging conditions. With the low and medium hydrogen charging conditions, the HE property of the L-Si specimen was higher than that of the As-OQ specimen, whereas their HE properties markedly declined to a similar level under the high hydrogen charging condition. The HE property of the L-Si specimen with increased dislocation-slip stability by applying stress relaxation was equivalent to that of the L-Si specimen under the high hydrogen charging condition. These results revealed that increasing dislocation-slip stability improved the HE property in the range of low to medium hydrogen charging. Under the high hydrogen charging condition, dislocation-slip stability did not contribute to improving the HE property, but it was found that the carbide precipitation morphology, particularly coarse carbides precipitated on prior γ grain boundaries, influenced the HE property.

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Hydrogen Content Dependence of the Contribution of Dislocation-slip Stability and Carbide Precipitation Morphology to the Hydrogen Embrittlement Property of High-strength Martensitic Steels

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Characterization of Crack Growth Acceleration of V-added Precipitation-strengthened High-Mn Austenitic Steel in High-pressure Gaseous Hydrogen Environment

Tatsuya Iwano, Atsushi Saji, Kodai Miura, Yukio Tachi, Osamu Takakuwa

pp. 1288-1300

DOI:

10.2355/tetsutohagane.TETSU-2024-093

Abstract

To verify the crack growth resistance of the V-added precipitation-strengthened high-Mn austenitic steel subject to a static and dynamic loading in a hydrogenated environment, the fracture toughness test and two types of fatigue crack growth (FCG) test, i.e., stress intensity factor range ΔK-increasing and ΔK-constant tests were performed under high-pressure gaseous hydrogen environment under the pressure of 95 MPa. The fracture toughness dramatically decreased from 95 to 35 MPa∙m1/2 by hydrogen occlusion. The fracture surface consists of intergranular fracture aspects in gaseous hydrogen despite being covered by the dimples tested in air. The FCG acceleration was also pronounced: more acceleration emerged as the ΔK became higher. When changing the loading frequency f as 1, 0.1, 0.01, and 0.001 Hz under constant ΔK of 30 MPa∙m1/2, the relative FCG rate in gaseous hydrogen to that in air became higher as f decreased, i.e., the dependency of FCG acceleration on the crack opening time. However, the acceleration did not completely depend on the crack opening time, which means a part of FCG acceleration was dominated by crack tip plasticity under cyclic loading. The scanning electron microscopy (SEM) characterization, including the electron-channeling contrast (ECC) imaging and the electron backscatter diffraction (EBSD) analysis, demonstrated that the crack preferentially propagates along grain boundary in the hydrogenated environment. The micro-void and/or micro-crack ahead of the primary FCG crack initiated at the M23C6 carbides precipitated at the grain boundary, which triggered the dramatic acceleration of FCG under 95 MPa gaseous hydrogen.

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Characterization of Crack Growth Acceleration of V-added Precipitation-strengthened High-Mn Austenitic Steel in High-pressure Gaseous Hydrogen Environment

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Yielding Behavior of Low Carbon Martensitic Steel Sheet Containing Retained Austenite

Junya Tobata, Hidekazu Minami, Yuki Toji, Shinjiro Kaneko

pp. 1301-1311

DOI:

10.2355/tetsutohagane.TETSU-2024-107

Abstract

Quenching and Partitioning (Q&P) steel sheets, which utilize the transformation induced plasticity (TRIP) effect of retained austenite to improve the elongation of high strength steel sheets, are expected to become an important material for next-generation automotive structural parts. Although it has been reported that the yield strength (YS) of the Q&P steels consisting of tempered martensitic microstructure with retained austenite (hereafter ”Q&P steels” in this study) is affected by retained austenite, the mechanism has not yet been discussed in detail. The purpose of this study is to clarify the effect of the carbon content in retained austenite on the yielding behavior of the Q&P steels. The chemical composition of the model steel used here was 0.18%C-1.5%Si-3.0%Mn (mass%). The steels were annealed at 1143 K, then cooled to 473 K, followed by holding at the temperatures between 523 K and 673 K for 600 s. The increased carbon content in retained austenite increased the YS of the Q&P steels. It was found that the yielding of the Q&P steels was caused by the stress-induced transformation of retained austenite when the critical stress for the stress-induced transformation was lower than the elastic limit of tempered martensitic matrix. This result revealed that the increased carbon content in retained austenite was able to achieve the higher elastic limit of martensitic steels containing retained austenite.

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Yielding Behavior of Low Carbon Martensitic Steel Sheet Containing Retained Austenite

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Erratum: Apparent Viscosity Measurement of Gas-liquid Multiphase Fluids by the Falling Ball Method [Tetsu-to-Hagané, Vol.110 (2024), No.6, pp.483-493]

pp. 1312-1313

DOI:

10.2355/tetsutohagane.110.1312
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Erratum: Apparent Viscosity Measurement of Gas-liquid Multiphase Fluids by the Falling Ball Method [Tetsu-to-Hagané, Vol.110 (2024), No.6, pp.483-493]

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