Fe-5Mn-0.1C中Mn鋼におけるリューダース変形中の微視組織および塑性の発達

小山 元道*; 山下 享介*; 諸岡 聡; 澤口 孝宏*; Yang, Z.*; 北條 智彦*; 川崎 卓郎; Harjo, S.

鉄と鋼, 110(3), p.197 - 204, 2024/02

https://doi.org/10.2355/tetsutohagane.TETSU-2023-038

The local plasticity and associated microstructure evolution in Fe-5Mn-0.1C medium-Mn steel (wt.%) were investigated in this study. Specifically, the micro-deformation mechanism during Lders banding was characterized based on multi-scale electron backscatter diffraction measurements and electron channeling contrast imaging. Similar to other medium-Mn steels, the Fe-5Mn-0.1C steel showed discontinuous macroscopic deformation, preferential plastic deformation in austenite, and deformation-induced martensitic transformation during Lders deformation. Hexagonal close-packed martensite was also observed as an intermediate phase. Furthermore, an in-situ neutron diffraction experiment revealed that the pre-existing body- centered cubic phase, which was mainly ferrite, was a minor deformation path, although ferrite was the major constituent phase.

残留オーステナイトを含有する中Mn複合組織鋼の高速変形特性

興津 貴隆*; 北條 智彦*; 諸岡 聡; 宮本 吾郎*

鉄と鋼, 110(3), p.260 - 267, 2024/02

https://doi.org/10.2355/tetsutohagane.TETSU-2023-065

We have investigated the dynamic tensile properties of 4, 5, 6-mass%-Mn-containing low carbon steels with multi-phase microstructures containing retained austenite. The five materials used were classified into two groups. The first group of materials, with around 10% of retained austenite, showed normal strain rete dependence of yield strength (YS) and tensile strength (TS) as in conventional high strength steels. The second group of materials, containing 25-36% of retained austenite, exhibited Lders elongation showed also normal strain rate dependence in YS and flow stress at Lders deformation, but TS varied in a complex manner. Among the second group, in the 4 Mn steel, TS was nearly constant at strain rates below 1 s but increased slightly at higher strain rates. In the 5 and 6 Mn steels, TS once decreased up to the strain rate of 1 or 10 s, and then began to increase at higher strain rates. These behaviors were discussed in terms of temperature rise during plastic deformation causing suppression of martensitic transformation, and thermal stability of retained austenite. In the 4 Mn steel with relatively unstable retained austenite, almost all the austenite transforms regardless of strain rate. In the 5 and 6 Mn steels, where the retained austenite is moderately stable, strain induced transformation of austenite continues up to high plastic strain, providing a good balance of strength and ductility. At high strain rate, TS decreases slightly due to temperature rise, but at higher strain rates than 1 s, the strain rate sensitivity of flow stress in ferrite become prominent and the flow stress increases.

Changes of dislocation density and dislocation arrangement during tensile deformation in lath martensitic steels

Harjo, S.; 川崎 卓郎; 諸岡 聡

Advanced Experimental Mechanics, 2, p.112 - 117, 2017/10

https://doi.org/10.11395/aem.2.0_112

To understand strengthening mechanism in lath martensitic steels, in situ neutron diffractions during tensile deformation for 22SiMn2TiB steel and Fe-18Ni alloy were performed using TAKUMI of J-PARC. Profile analyses were performed using Convolutional Multiple Whole Profile (CMWP) fitting and Williamson-Hall (W-H) methods. As results, the dislocation densities as high as 10 m in the as-quenched states of both steels were determined hardly to change or slightly increase by the CMWP method. The reliability of the dislocation density obtained from the W-H method was low, because the whole profile was not considered for the analysis. In the former method, the values of parameter M related to dislocations arrangement was found to decrease rapidly for both steels at the beginning of plastic deformation. Hence, high work hardening in the lath martensitic steels was considered due to the dislocations rearrangements with plastic deformation.

Compatibility of reduced activation ferritic/martensitic steel specimens with liquid Na and NaK in irradiation rig of IFMIF

湯谷 順明*; 中村 博雄; 杉本 昌義

JAERI-Tech 2005-036, 10 Pages, 2005/06

JAERI-Tech-2005-036.pdf:2.06MB

材料の照射特性は温度依存性が強いため、照射中の試料温度測定は重要である。しかしながら、中性子照射損傷が20dpa/年以上となるIFMIFの高中性子束領域において、鉄ベースの合金を照射する場合、大量の核発熱が生じるため、試料温度を正確に計測することは、不活性ガスを照射試料と試料ホルダーとの間のギャップに充てんして試料温度を試料ホルダーに埋め込んだ熱電対によって測定する従来の方式では、照射中にギャップの熱伝達率が変化するため極めて困難である。その対策としてギャップの熱伝達率がより安定と期待される液体金属(ナトリウム又はナトリウム-カリウム合金)をギャップに充てんする方法が提案(FZKが提案)されているが、液体金属と低放射化フェライト鋼との両立性に懸念があった。本報告は、このような液体金属と低放射化フェライト鋼との両立性について検討し、照射リグ設計への提案として、充てん前の液体金属の純度管理や炭素原子移行を予防する材質選択上の注意を述べる。

Mechanical properties and microstructure of F82H steel doped with boron or boron and nitrogen as a function of heat treatment

若井 栄一; 佐藤 通隆*; 沢井 友次; 芝 清之; 實川 資朗

Materials Transactions, 45(2), p.407 - 410, 2004/01

https://doi.org/10.2320/matertrans.45.407

材料中に生成するHeが組織や強度特性に及ぼす影響を評価するために原子炉での熱中性子とのB(n,)Li反応を利用したB添加法がある。本研究ではFe-8Cr-2W-0.1C系のマルテンサイト鋼F82Hに約60ppmのBを添加させた材料と約60ppmのBと約200ppmのNを複合添加させた材料を作製し、その組織と強度特性を評価した。これらの試料の熱処理はBの偏析を防ぐために950Cから1150Cまでの数種類の温度で約30分間焼ならしを行った後、水中に急冷した。その後、約780Cで30分間焼きもどしを行った。これらの熱処理後、各試料の組織やSIMSによってBやNの分布を調べるとともに、引張試験とシャルピー衝撃試験等を行った。B添加材とB+N複合添加材の引張特性は添加していない材料とほぼ同一であったが、衝撃試験では無添加材に比べてB添加材の延性脆性遷移温度(DBTT)が3070C程度上昇したのに対して、BとNを複合添加した材料ではDBTTは上昇しなかった。また、この複合添加材ではBの偏りを抑えることができた。また、焼ならし温度によってもBの偏析分布やDBTTが変化した。以上の結果から材料中にHeをより均一に生成させるためにはBとNを複合添加し、1000Cで焼きならしをした材料が最適であることがわかった。

拡大核融合炉・材料研究合同委員会報告書; 2001年7月16日、東京

核融合炉研究委員会; 核融合材料研究委員会

JAERI-Review 2002-008, 79 Pages, 2002/03

JAERI-Review-2002-008.pdf:9.92MB

拡大核融合炉・材料研究合同委員会が、2001年7月16日に、東京で開催された。この合同委員会では、原研及び大学におけるブランケット、材料及び国際核融合材料照射施設(IFMIF)の開発計画と開発の現状に関する報告が行われるとともに、今後の原研と大学の協力に関する議論が行われた。本報告書は、本合同委員会で用いられた資料及びそのまとめから構成されている。

Multi-scale in situ characterization of micro-deformation during Lders band propagation in a medium Mn steel

小山 元道*; 山下 享介*; 諸岡 聡; Yang, Z.*; Varanasi, R.*; 北條 智彦*; 川崎 卓郎; Harjo, S.

no journal, , 

The micro-deformation of an Fe-5Mn-0.1C medium Mn steel consisting of face-centered cubic and body-centered cubic phases was characterized through multi-scale in situ scanning electron microscopy. Specifically, multiscale in situ back-scatter electron imaging coupled with ex situ electron backscatter diffraction measurements was conducted under tensile testing. The Fe-Mn-C alloy showed macroscopically localized deformation (i.e., Lders deformation), and the deformation-localized region consisted of multiple find deformation bands. The hierarchical structure of the deformation bands initiated from a specimen side edge and propagated to the other side edge. More microscopically, the plastic deformation preferentially progressed in a face-centered cubic phase, and temporarily stopped when the fine deformation band encountered a group of body-centered cubic grains, which resulted in zigzag propagation of the fine deformation bands. Through coalescence of fine deformation bands, a thick macroscopic deformation band formed. By repetition of the micro-deformation process, the thick deformation band front moved along the tensile direction from an end of the gauge portion to the other end.