US20170101702A1 - Metallic glass composites with controllable work-hardening capacity - Google Patents

Metallic glass composites with controllable work-hardening capacity Download PDF

Info

Publication number
US20170101702A1
US20170101702A1 US15/287,693 US201615287693A US2017101702A1 US 20170101702 A1 US20170101702 A1 US 20170101702A1 US 201615287693 A US201615287693 A US 201615287693A US 2017101702 A1 US2017101702 A1 US 2017101702A1
Authority
US
United States
Prior art keywords
phase
metallic glass
metastable
work
transformable
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Abandoned
Application number
US15/287,693
Other languages
English (en)
Inventor
Eun Soo Park
Wookha RYU
Hyun Seok Oh
Jinwoo Kim
So Yeon Kim
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
SNU R&DB Foundation
Original Assignee
Seoul National University R&DB Foundation
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Seoul National University R&DB Foundation filed Critical Seoul National University R&DB Foundation
Assigned to SEOUL NATIONAL UNIVERSITY R&DB FOUNDATION reassignment SEOUL NATIONAL UNIVERSITY R&DB FOUNDATION ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: KIM, SO YEON, OH, HYUN SEOK, PARK, EUN SOO, RYU, WOOKHA, KIM, JINWOO
Publication of US20170101702A1 publication Critical patent/US20170101702A1/en
Priority to US16/106,232 priority Critical patent/US10895005B2/en
Abandoned legal-status Critical Current

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C45/00—Amorphous alloys
    • C22C45/10—Amorphous alloys with molybdenum, tungsten, niobium, tantalum, titanium, or zirconium or Hf as the major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/11—Making amorphous alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C45/00—Amorphous alloys
    • C22C45/001—Amorphous alloys with Cu as the major constituent

Definitions

  • the carbide reacted with various additives such as silicon (Si), chromium (Cr), titanium (Ti), vanadium (V), tantalum (Ta), molybdenum (Mo), zirconium (Zr), boron (B), calcium (Ca), and the like, to exist in a titanium grain boundary, such that strength was significantly improved, but elongation tended to be decreased, such that toughness was not largely improved.
  • a technology for a titanium/aluminum composite in which a ceramic reinforcement material is inserted has been disclosed in Korean Patent Nos. 10-0564260 and 10-1197581, but there were limitations in that an effect of improving strength was excellent, but toughness was not improved.
  • a phase transformation alloy shape memory alloy or super-elastic alloy is a material capable of significantly improving toughness through martensitic transformation under specific temperature and stress conditions.
  • phase transformation alloy causes a large strain hardening section after phase transformation by partially consuming energy applied from the outside at the time of phase transformation as phase transformation energy and preventing stress concentration through a plurality of shear bands formed by interactions with a metallic glass matrix, thereby having a deformation behavior similar to a work-hardening behavior of a crystalline material.
  • An exemplary embodiment of the present invention provides a metallic glass matrix composite capable of systemically controlling work-hardening capacity thereof by controlling physical properties of a second phase and adjusting a volume fraction of a phase, while implementing post-yield work-hardening by allowing a metastable second phase of which phase tranformation from an austenite B2 phase to a martensite phase may occur to be precipitated in-situ in a metallic glass matrix by polymorphic phase transformation during a solidification process without a separate synthetic process.
  • An exemplary embodiment of the present invention provides a metallic glass matrix composite capable of adjusting a volume fraction of a second phase in the composite through casting process control due to fixed correlation between physical properties (absorbed energy, a phase transformation temperature, and hardness) of a precipitated second phase and absorbed energy per unit volume fraction of the second phase to control work-hardening caapcity.
  • Another embodiment of the present invention provides a metallic glass matrix composite capable of preventing brittle fracture of a metallic glass alloy matrix by decreasing concentration of stress applied to a material during a deformation process through phase transformation of a metastable second phase precipitated in the metallic glass matrix by polymorphic phase transformation during a solidification without a separate synthetic process into a stable phase, and capable of having a large strain hardening section after phase transformation to improve toughness through a work-hardening behavior.
  • a crystalline metastable second phase formed through polymorphic phase transformation may be precipitated, such that work-hardening for improving toughness of metallic galss through phase transformation of the metastable second phase occuring at the time of deformation may be performed.
  • the second phase formed by polymorphic phase transformation during the solidification may have a composition similar to that of the matrix as a metastable phase generally formed in a rapid cooling process, and has a tendency to be phase-transformed into a stable phase.
  • the crystalline metastable phase may serve as a phase transformation media of which a phase is transformed at the time of deformation of the material, and phase transformation of the crystalline metastable phase may serve as a mechanism relaxing stress applied to the material to inhibit concentration of the stress, thereby preventing brittle fracture of the metallic glass matrix.
  • work-hardening capacity of the composite may be controlled by finally measuring the physical properties (absorbed energy E t a , a phase transformation temperature h Ms , or a hardness H 2nd ) of the second phase in the metallic glass matrix to calculate absorbed energy by work-hardening per unit volume fraction of the second phase, and adjusting the volume fractrion of the second phase in the composite through casting process control.
  • the absorbed energy (J/cm 3 ⁇ vol %) by work-hardening per unit volume fraction of the phase-transformable metastable second phase (J/cm 3 ⁇ vol %) may be calculated usign the following Equation, and an effect caused by the volume fraction of the second phase may be excluded.
  • V p ( ⁇ ⁇ y ⁇ f ⁇ ( ⁇ - ⁇ y ) ⁇ ⁇ ⁇ - ( ⁇ f - ⁇ y ) 2 2 ⁇ ⁇ ) / V f
  • the process conditions controlled according to the exemplary embodiment of the present invention may be three, that is, an output power of arc plasma, a gas pressure when a molten metal is injected into a mold, and a cooling capacity through the mold. More specifically, the output power of the arc plasma may be determined by adjusting an output voltage and an output current, and the higher the output power, the higher the volume fraction of the second phase. In addition, the higher the gas pressure, the lower the volume fraction of the seocnd phase. Further, the cooling capacity may be changed depending on a diameter and a shape of the mold, water cooling, or the like, and the thickner the test sample prepared in the mold, the lower the cooling capacity and the higher the volume fraction of the second phase. Therefore, the metallic glass matrix composite with controllable work-hardening capacity may be prepared by adjusting the deduced E q a,V value and the volume fraction of through the casting process control.
  • the metallic glass matrix composite having a structure in which the metastable second phase is precipitated in the metallic glass matrix by polymorphic phase transformation may be provided without a separate additional process.
  • the metallic glass matrix composite according to the present invention may prevent brittle fracture of the metallic glass matrix by stress relaxation and large strain hardening behavior accompanied when the metastable second phase precipiated by polymorphic phase transformation is transforemd into the stable phase, thereby making it possible to significantly improve toughness.
  • a prepartion method of the metallic glass matrix composite according to the present invention which is a method capable of starting from a mother element metal, which is a raw material, to complete the alloying and production of the composite in a single process, may significantly decrease a cost and production time as compared to a multi-step composite preparation method using the existing metal power, which is complicated and requires a large cost.
  • Equations suggested according to the exemplary embodiment of the present invention includes only the absorbed energy E t a , the phase transformation temperature T Ms , or the hardness H 2nd as variables, these Equations may be utilized in main Equations and evaluation methods in computer simulations, and the like, for effectively controlling work-hardening capacity of the composite by controlling physical properties of the second phase.
  • work-hardening capacity of the composite may be easily controlled by effectively adjusting the volume fraction fo the phase-transformable metastable second phase in the metallic glass mnaterix in the alloy system in the boundary composition region in which the crstalline metastable phase and the bulk metallic glass may be formed.
  • FIG. 2 is a differential scanning calorimetry result illustrating an effect of adding Si to the Ti—Cu—Ni alloy.
  • FIG. 3 is a scanning electron microscope (SEM) photograph of a test sample prepared according to an exemplary embodiment of the present invention and a graph illustrating X-ray diffraction analysis result thereof.
  • FIG. 4 is a result obtained by observing cross-sectional micro-structure of metallic glass matrix composites having various volume fractions of a second phase, prepared by adjusting an arc plasma current in a Ti 48 Cu 40 Ni 7 Si 1 Sn 2 Zr 2 alloy composition according to an exemplary embodiment of the present invention using an optical microscope.
  • FIG. 5 illustrates a stress-strain diagram obtained by performing a uniaxial compression test on the metallic glass matrix composites having various volume fractions of the second phase, illustrated in FIG. 4 .
  • T Ms martensite-start temperature
  • a metallic glass matrix composite according to the present exemplary embodiment is composed of a Ti—Cu—Ni—Si based metallic glass matrix and a metastable second phase precipated by polymorphic phase transformation.
  • the second phase formed by polymorphic phase transformation during a solidification process which is a metastable phase having a composition similar to a matrix composition, tends to be changed to a stable phase by an external temperature or stress. Due to characteristics of the metatable phase, the metastable phase serves as a phase transformation media at the time of deformation of a material, phase transformation of a crystalline metastable phase as described above serves as a mechanism of relaxing stress applied to the material, thereby preventing brittle fracture of the metallic glass matrix.
  • the present inventors developed a metallic glass composite having excellent strength and toughness due to work-hardening characteristics obtained by precipitating a phase-transformable crystalline metastable second phase by stress in a high-strength Ti based metallic glass matrix through polymorphic phase transformation of a matrix metal caused by metal solidification.
  • a ternary eutectic composition represented by Composition Formula, Ti 50 Cu 42 Ni 8 may be determined as a base composition by evaluating glass forming ability in various compositions with respect to ternary alloys composed of Ti, Cu, and Ni.
  • FIG. 2 is a differential scanning calorimetry result illustrating an effect of adding Si to the Ti—Cu—Ni alloy. Glass forming ability is excellent in a Ti 50 Cu 42 Ni 8 ternary alloy composition region, but it is impossible to precipiate a single metastable second phase by polymorphic phase transformation through polymorphic precipitation during a solidification process. However, as illustrated in FIG. 2 , it may be confirmed that as a small amount of Si is added to the alloy composition region, a stable region of a phase-transformable metastable B2 phase is expanded, such that the B2 phase may be precipitated alone by polymorphic phase transformation during solidification.
  • the present inventors developed an alloy composition which has excellent glass forming ability and in which a metal stable B2 second phase may be precipiated by polymorphic phase transformation by adding Si at a content of about 0.5 at % or more based on the Ti 50 Cu 42 Ni 8 alloy composition.
  • a metal stable B2 second phase may be precipiated by polymorphic phase transformation by adding Si at a content of about 0.5 at % or more based on the Ti 50 Cu 42 Ni 8 alloy composition.
  • the content of added Si is more than 5 at %, glass forming ability is rapidly deteriorated, such that it become difficult to prepare a composite even by adjusting a cooling rate.
  • a and a indicate a metallic glass phase, wherein A indicates a metallic glass phase of which a volume fraction is large and a indicates a metallic glass phase of which a volume fraction is small, and C and c indicate cystalline phase, wherein C indicates a crystaline phase of which a volume fraction is large and c indicates a crystalline phase of which a volume fraction is small.
  • C indicates a crystaline phase of which a volume fraction is large and c indicates a crystalline phase of which a volume fraction is small.
  • FIG. 3 is a scanning electron microscope (SEM) photograph of a test sample prepared according to an exemplary embodiment of the present invention and a graph illustrating X-ray diffraction analysis result thereof.
  • the test sample has a Ti 48 Cu 40 Ni 7 Si 1 Sn 2 Zr 2 composition, and it may be confirmed that the test the test sampe is composed of a matrix portion having a light color and a precipiation portion having a dark color in the SEM photograph.
  • the matrix portion is a metallic glass phase
  • the precipitation portion which is a crystalline phase
  • FIG. 4 is an optical microscope photograph illustrating cross sections of metallic glass matrix composites having various volume fractions of a second phase, prepared using a Ti 48 Cu 40 Ni 7 Si 1 Sn 2 Zr 2 composition among alloys according to an exemplary embodiment of the present invention.
  • a metastable B2 second phase of which absorbed energy (E t a ) and T Ms were the same as each other was precipitated.
  • the reason may be that a melting temperature and flowability of a molten metal are changed depending on the output power (output voltage: about 5 to 50 V, output current; about 30 to 300 A), and thus, a supercooling degree at the time of solidification is changed, which affects formation of the metasatble B2 second phase formed by allotropic transformation in the metallic glass matrix.
  • the output power is excessively low (the output voltage is less than about 5 V or the output current is less than about 30 A)
  • output power is excessively high (the output voltage is more than about 50 V or the output current is more than about 300 A)
  • a change in composition may occur due to vaporization of a consitution element in the material.
  • a cooling rate condition having a large influence on glass forming ability of the alloy may also have a signficant influence on controlling the volume fraction of the composite, and in the case of the alloy composition according to the presetn invention, it is preferable to perform the casting while adjusting cooling capacity in a range of about 10 1 -10 4 K/s in consideration of glass forming ability.
  • FIG. 5 illustrates a stress-strain diagram obtained by performing a uniaxial compression test on the metallic glass matrix composites illustrated in FIG. 4 .
  • the metallic glass matrix composite has mechanical properties similar to those of metallic glass having brittleness, there is almost no work-hardening capacity, but as the volume fraction of the second phase, the work-hardening capacity of the composite is increased with a constant tendency.
  • FIG. 6 is a high-energy X-ray diffraction analysis result illustrating a real-time phase transformation behavior at the time of compressing a composite test sample prepared using the Ti 48 Cu 40 Ni 7 Si 1 Sn 2 Zr 2 alloy composition.
  • structure analysis using high-energy X-ray it is easy to observe phase transformation in a bulk type test sample due to high permeability, and a phase transformation behavior of about 3 mm bulk test sample prepared according to the present exemplary embodiment at the time of compression was real-time analyzed usig the characteristics as described above.
  • phase transformation to a martensite phase occurred under a compression stress of about 1900 MPa (in the vicinity of a yield point of the material). This is clearly observed in both a vertical direction (left) and a horizontal direction (right) of the high-energy X-ray beam.
  • absorbed energy obtained by deformation (work-hardening) after first yielding of the metallic glass matrix composite containg the phase-transformable metastable B2 phase is calculated using Equation
  • V p ( ⁇ ⁇ y ⁇ f ⁇ ( ⁇ - ⁇ y ) ⁇ ⁇ ⁇ - ( ⁇ f - ⁇ y ) 2 2 ⁇ ⁇ ) / V f
  • the absorobed energy of the phase-transformable B2 second phase is obtained by integrating the stress-strain diagram obtained by performing a compression test on an alloy prepared as a single B2 cystalline phase.
  • FIG. 9 as the absorobed energy of the phase-transformable B2 second phase is increased, absorbed energy of the composite containing a second phase thereof by work-hardening is increased, and thus, plastic deformability is large.
  • Work-hardening capacity of the composite may be controlled by measuring the absorbed energy (E t a ), which is one of the physical properties, of the phase-transformable metastable B2 second phase precipated in the composite to calculate absorbed energy (E p a,V ) by work-hardening per unit volume fraction of the second phase formed in the metallic glass matrix composite prepared using each of the compositions.
  • E t a the absorbed energy
  • E p a,V absorbed energy
  • T Ms martensite-start temperature
  • H 2nd hardness
  • E p a,V absorbed energy
  • Work-hardening capacity of the composite may be controlled by measuring hardness, which is one of the physical properties, of the phase-transformable metastable B2 second phase precipitated in the composite and calculate the absorbed energy (E p a,V ) by work-hardening per unit volume fraction of the second phase formed in the metallic glass matrix composite prepared using each of the compositions.
  • hardness which is one of the physical properties
  • work-hardening capacity of the composite may be controlled by calculating the absorbed energy (E p a,V ) by work-hardening per unit volume fraction of the second phase formed in the metallic glass matrix composite prepared using each of the compositions.
  • a metallic glass matrix composite with controllable work-hardening capacity capable of having significantly excellent toughness due to the metastable second phase precipitated in-situ in the metallic glass matrix by polymorphic phase transformation during the solidification process without a separate synthetic process, and capable of controlling work-hardening capacity by adjusting the volume fraction of the second phase in the composite through measurement of the physical properties of the metastable B2 second phase and casting process control due to constant correlation between the physical properties (the absorbed energy E t a , the phase transformation temperature T Ms , or the hardness H 2nd ) of the metastable B2 second phase precipated in the metallic glass matrix in the related composition region and the absorbed energy (E p a,V ) by work-hardening per unit volume fraction of the second phase in the metallic glass matrix.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Analysing Materials By The Use Of Radiation (AREA)
  • Manufacture Of Alloys Or Alloy Compounds (AREA)
US15/287,693 2015-10-07 2016-10-06 Metallic glass composites with controllable work-hardening capacity Abandoned US20170101702A1 (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
US16/106,232 US10895005B2 (en) 2015-10-07 2018-08-21 Metallic glass composites with controllable work-hardening capacity

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
KR10-2015-0141240 2015-10-07
KR1020150141240A KR101752976B1 (ko) 2015-10-07 2015-10-07 가공경화능 제어 비정질 합금 기지 복합재의 제조 방법 및 그에 따라 제조된 복합재

Related Child Applications (1)

Application Number Title Priority Date Filing Date
US16/106,232 Continuation US10895005B2 (en) 2015-10-07 2018-08-21 Metallic glass composites with controllable work-hardening capacity

Publications (1)

Publication Number Publication Date
US20170101702A1 true US20170101702A1 (en) 2017-04-13

Family

ID=58499725

Family Applications (2)

Application Number Title Priority Date Filing Date
US15/287,693 Abandoned US20170101702A1 (en) 2015-10-07 2016-10-06 Metallic glass composites with controllable work-hardening capacity
US16/106,232 Active 2037-04-09 US10895005B2 (en) 2015-10-07 2018-08-21 Metallic glass composites with controllable work-hardening capacity

Family Applications After (1)

Application Number Title Priority Date Filing Date
US16/106,232 Active 2037-04-09 US10895005B2 (en) 2015-10-07 2018-08-21 Metallic glass composites with controllable work-hardening capacity

Country Status (2)

Country Link
US (2) US20170101702A1 (ko)
KR (1) KR101752976B1 (ko)

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20180282845A1 (en) * 2017-03-29 2018-10-04 Yonsei University, University-Industry Foundation (UIF) Metal alloy composition, method of fabricating the same, and product comprising the same
CN112380690A (zh) * 2020-11-11 2021-02-19 安徽工业大学 一种亚稳复相金属材料流变应力模型的构建方法
US11214854B2 (en) * 2017-08-18 2022-01-04 Heraeus Deutschland GmbH & Co. KG Copper-based alloy for the production of bulk metallic glasses

Families Citing this family (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR102098303B1 (ko) * 2017-03-29 2020-04-07 연세대학교 산학협력단 금속 합금 조성물, 그 제조 방법, 및 이를 포함하는 성형품
CN110323980B (zh) * 2019-06-29 2021-04-30 宁波宁变电力科技股份有限公司 移相调压方法、调压开关及具有该调压开关的变压器

Family Cites Families (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US6264719B1 (en) 1997-08-19 2001-07-24 Titanox Developments Limited Titanium alloy based dispersion-strengthened composites
KR100448152B1 (ko) 2001-12-17 2004-09-09 학교법인연세대학교 연성의 입자가 강화된 비정질 기지 복합재 및 그의 제조방법
KR100513584B1 (ko) 2003-03-31 2005-09-09 현대자동차주식회사 연성이 우수한 고강도 마그네슘 복합재료와 그 제조방법
JP5148820B2 (ja) 2005-09-07 2013-02-20 株式会社イーアンドエフ チタン合金複合材料およびその製造方法
KR100723162B1 (ko) 2005-12-24 2007-05-30 주식회사 포스코 고강도 고인성을 갖는 결정-비정질 복합재료
KR101197581B1 (ko) 2009-12-09 2012-11-06 연세대학교 산학협력단 금속기지 복합재 및 그 제조 방법
KR20130110689A (ko) 2012-03-30 2013-10-10 서울대학교산학협력단 가공경화가 가능한 비정질 금속 기지 복합재료
KR20130142467A (ko) 2012-06-19 2013-12-30 한국과학기술연구원 티타늄계 벌크 비정질 매트릭스 복합체 및 그 제조 방법
CN102978541B (zh) * 2012-12-14 2015-01-07 兰州理工大学 形状记忆晶相强韧化Ti基非晶复合材料及其制备方法
KR101908962B1 (ko) 2013-12-27 2018-12-10 서울대학교 산학협력단 가공경화가 가능한 비정질 합금 기지 복합재료의 제조방법
JP5703414B1 (ja) * 2014-09-10 2015-04-22 石福金属興業株式会社 白金族基合金の製造方法
KR101532409B1 (ko) * 2014-09-22 2015-06-30 서울대학교산학협력단 가공경화가 가능한 비정질 금속 기지 복합재료
KR101608614B1 (ko) 2015-01-16 2016-04-12 서울대학교산학협력단 가공경화능 제어 비정질 합금 기지 복합재의 제조방법 및 그에 따라 제조된 복합재료
CN104911512A (zh) * 2015-04-17 2015-09-16 辽宁工业大学 一种用枝晶增强钛基金属玻璃复合材料和纯钛制备双金属复合板的方法

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20180282845A1 (en) * 2017-03-29 2018-10-04 Yonsei University, University-Industry Foundation (UIF) Metal alloy composition, method of fabricating the same, and product comprising the same
US11214854B2 (en) * 2017-08-18 2022-01-04 Heraeus Deutschland GmbH & Co. KG Copper-based alloy for the production of bulk metallic glasses
CN112380690A (zh) * 2020-11-11 2021-02-19 安徽工业大学 一种亚稳复相金属材料流变应力模型的构建方法

Also Published As

Publication number Publication date
KR20170041594A (ko) 2017-04-17
US10895005B2 (en) 2021-01-19
KR101752976B1 (ko) 2017-07-11
US20190062884A1 (en) 2019-02-28

Similar Documents

Publication Publication Date Title
US10895005B2 (en) Metallic glass composites with controllable work-hardening capacity
BR112018075617B1 (pt) Aço para preparação de um molde para formação de plásticos, pó pré-formado para formar liga, seu uso, e artigo
JP6332570B1 (ja) 熱間圧延鋼板および鋼製鍛造部品ならびにそれらの製造方法
US20080298999A1 (en) Method for Producing a Copper Alloy Having a High Damping Capacity
KR101909839B1 (ko) 강재 및 그 제조 방법
US20150147225A1 (en) Beta-type titanium alloy having low elastic modulus and high strength
JP4424503B2 (ja) 棒鋼・線材
JP2014517875A (ja) 静的微細化及び動的強化でモーダル構造体化された鋼のクラス
JP3753101B2 (ja) 高強度高剛性鋼及びその製造方法
JP6332571B1 (ja) 熱間圧延鋼板および鋼製鍛造部品ならびにそれらの製造方法
US9790577B2 (en) Ti—Al-based alloy ingot having ductility at room temperature
Aranda et al. Effect of Mo on high entropy Ti-Nb-Zr-Ta alloy: Phase equilibria, microstructure and mechanical properties
KR20190034281A (ko) 열연 강판
JP5064356B2 (ja) 高強度で成形性に優れたチタン合金板およびチタン合金板の製造方法
Yin Development of cost-effective high-entropy alloys with superior mechanical properties
JP2019173160A (ja) 耐水素脆化特性に優れた低合金鋼
Campo et al. Directional Solidification of the Al0. 8CrFeNi2. 2 Eutectic High-Entropy Alloy
JP6504807B2 (ja) 塑性加工用または鋳造用高ヤング率低熱膨張合金およびその製造方法
KR20140118304A (ko) Ａｌ-Ｍｇ-Ｓｉ계 합금의 전위밀도 저감 방법 및 이를 이용한 Ａｌ-Ｍｇ-Ｓｉ계 합금 제조 방법
US20040256031A1 (en) Cu-based amorphous matrix composite materials containing high fusion point element and production method thereof
Biletska et al. Fabrication of an in situ bulk metallic glass composite with high magnesium content
Wieczerzak et al. Experimental and thermodynamic study of selected in-situ composites from the Fe-Cr-Ni-Mo-C system
Lucaci et al. Studies on Fe-Cr-Ni-Si-B bulk metallic glass for automotive applications
JP2003321741A (ja) 高温リラクセーション特性に優れた高強度ｐｃ鋼棒およびその製造方法
JP2021514029A (ja) 新しい二相ステンレス鋼

Legal Events

Date Code Title Description
AS Assignment

Owner name: SEOUL NATIONAL UNIVERSITY R&DB FOUNDATION, KOREA,

Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNORS:PARK, EUN SOO;RYU, WOOKHA;OH, HYUN SEOK;AND OTHERS;SIGNING DATES FROM 20161004 TO 20161005;REEL/FRAME:039962/0450

STCB Information on status: application discontinuation

Free format text: ABANDONED -- FAILURE TO RESPOND TO AN OFFICE ACTION