| {"qid":"96b8d00d-06e3-41bd-8246-1c73a1f2f70d","paper_id":"10.1002@adma.201807142","composition":"VCoNi","tag":"material phases","question_type":"long_answer","question":"Was VCoNi equiatomic alloy tested experimentally, and if so, what material phases were identified during characterization?","ground_truth_answer":"The VCoNi equiatomic alloy was experimentally tested and found to consist of a single face-centered cubic (fcc) phase structure with a lattice parameter of 0.3601 nm. XRD, TEM, and STEM analyses confirmed the alloy was devoid of precipitates and ordered phases, both in the matrix and at grain boundaries.","page_reference":"2","key_passage":"The alloy consists of a single fcc phase structure with a lattice parameter of 0.3601 nm. An electron backscatter diffraction (EBSD) inverse pole figure (IPF) map in Figure 1a shows recrystallized fcc grains with an average size of 5.64 ± 3.05 µm. The representative transmission electron microscopy (TEM) micrograph in Figure 1b and selected-area diffraction (SAD) patterns inset in Figure 1b show that the alloy is devoid of precipitates and ordered phases.","citation":"sohn2018ultrastrong","expected_retrieval":true} | |
| {"qid":"3fdeeee5-6405-47c7-852e-e796696527b2","paper_id":"10.1002@adma.201807142","composition":"VCoNi","tag":"experimental details","question_type":"long_answer","question":"How was the experimental VCoNi equiatomic alloy prepared and processed?","ground_truth_answer":"The VCoNi equiatomic alloy was fabricated using vacuum induction melting under argon atmosphere. The ingots were homogenized at 1200°C for 24h and cold-rolled to 75% reduction to produce 1.8mm thick sheets. The rolled sheets were then recrystallized at temperatures between 900-1200°C for 1-60 minutes followed by immediate water quenching.","page_reference":"2","key_passage":"The VCoNi equiatomic alloy was fabricated in a vacuum induction melting furnace under argon atmosphere. Ingots were homogenized at 1200 °C for 24 h and cold-rolled (reduction ratio; 75%) to produce 1.8 mm thick sheets. The rolled sheets were then recrystallized at 900–1200 °C for 1–60 min and immediately water-quenched.","citation":"sohn2018ultrastrong","expected_retrieval":true} | |
| {"qid":"70b896f8-63b3-4b1f-bd46-173ccc80a3e7","paper_id":"10.1002@adma.201807142","composition":"VCoNi","tag":"experimental results","question_type":"long_answer","question":"What were the main mechanical property results obtained from testing the VCoNi equiatomic alloy?","ground_truth_answer":"The fine-grained VCoNi alloy (2.0 ± 1.5 μm grain size) achieved a yield strength of nearly 1 GPa while maintaining good ductility with 38% total elongation and ultimate tensile strength of 1359 MPa. The alloy showed high strain hardening capability and an exceptionally high lattice friction stress of 383 MPa, which is almost three times higher than previous medium/high-entropy alloys and conventional austenitic steels.","page_reference":"3","key_passage":"Of particular significance is that the fine-grained VCoNi alloy (grain size of 2.0 ± 1.5 µm) reaches a yield strength of nearly 1 GPa despite being in a single fcc solid solution state. In addition, the alloy shows an ultimate tensile strength of 1359 MPa and a large total elongation of 38%, revealing also high strain hardening capability.","citation":"sohn2018ultrastrong","expected_retrieval":true} | |
| {"qid":"88c1a00b-1840-481c-b437-2e2db4cd080b","paper_id":"10.1002@adma.201807142","composition":"Ti30Cr40Mn30","tag":"material phases","question_type":"long_answer","question":"Was Ti30Cr40Mn30 tested experimentally, and if so, which material phases were identified during experiments?","ground_truth_answer":"Insufficient information to answer - this composition is not discussed in the paper","page_reference":"N/A","key_passage":"Composition not found in the literature","citation":"sohn2018ultrastrong","expected_retrieval":false} | |
| {"qid":"642b8ff0-bcf4-4904-b732-a2e9d8f4097c","paper_id":"10.1002@adma.201807142","composition":"Ti30Cr40Mn30","tag":"experimental details","question_type":"long_answer","question":"Based on literature, how were Ti30Cr40Mn30 specimens prepared for experimental characterization?","ground_truth_answer":"Insufficient information to answer - this composition is not discussed in the paper","page_reference":"N/A","key_passage":"Composition not found in the literature","citation":"sohn2018ultrastrong","expected_retrieval":false} | |
| {"qid":"fe925042-0c0c-4c0c-8a06-4caef05787c9","paper_id":"10.1002@adma.201807142","composition":"Ti30Cr40Mn30","tag":"experimental results","question_type":"long_answer","question":"If Ti30Cr40Mn30 was tested, what were the main findings regarding its mechanical properties?","ground_truth_answer":"Insufficient information to answer - this composition is not discussed in the paper","page_reference":"N/A","key_passage":"Composition not found in the literature","citation":"sohn2018ultrastrong","expected_retrieval":false} | |
| {"qid":"5ed49034-9601-4dcc-b2ac-b0ece9fe9327","paper_id":"10.1007@s00339-019-2506-z","composition":"Co30Cr10Fe10Al18Ni32-xMox (x=0, 1, 2, 3)","tag":"material phases","question_type":"long_answer","question":"Was Co30Cr10Fe10Al18Ni32-xMox (x=0, 1, 2, 3) tested experimentally, and if so what phases were identified in the alloy system?","ground_truth_answer":"The alloy system consisted of face-centered cubic (FCC) and body-centered cubic (BCC) phases. Mo0 exhibited a complete eutectic microstructure, while Mo1, Mo2, and Mo3 alloys contained primary BCC phase and eutectic phases. Mo acted as a solid solution strengthening element in both FCC and BCC phases, with a solubility limit of around 3 at.% in the FCC phase.","page_reference":"pages 2-3","key_passage":"The XRD patterns of Co30Cr10Fe10Al18Ni32−xMox alloys are presented in Fig. 1. [...] The information shows that all alloys consist of FCC and BCC phases.","citation":"yang2019enhancing","expected_retrieval":true} | |
| {"qid":"dd1f65b6-13b7-4442-a4be-937ef1d288b5","paper_id":"10.1007@s00339-019-2506-z","composition":"Co30Cr10Fe10Al18Ni32-xMox (x=0, 1, 2, 3)","tag":"experimental details","question_type":"long_answer","question":"How were the Co30Cr10Fe10Al18Ni32-xMox (x=0, 1, 2, 3) specimens prepared for experimental testing?","ground_truth_answer":"The alloys were prepared by arc melting under high-purity argon atmosphere using elements with purity above 99.9 wt%. The ingots were re-melted four times to improve homogeneity and cast in a copper mold (80mm length, 10mm width, 2mm thickness). Samples for microstructure analysis were cut using electronspark wire cutting, followed by grinding, polishing and corrosion in aqua regia solution.","page_reference":"page 2","key_passage":"Five multi-principal component alloys with a small content of Mo, Co30Cr10Fe10Al18Ni32−xMox (x=0, 1, 2, 3, in molar ratio, denoted as Mo0, Mo1, Mo2, Mo3) were prepared by arc melting under a high-purity argon atmosphere simultaneously.","citation":"yang2019enhancing","expected_retrieval":true} | |
| {"qid":"0230a8ca-a80e-467e-acc7-05603c78702a","paper_id":"10.1007@s00339-019-2506-z","composition":"Co30Cr10Fe10Al18Ni32-xMox (x=0, 1, 2, 3)","tag":"experimental results","question_type":"long_answer","question":"What were the main mechanical property findings from testing Co30Cr10Fe10Al18Ni32-xMox (x=0, 1, 2, 3)?","ground_truth_answer":"The Mo2 alloy showed the best mechanical properties with the highest fracture tensile strength of 1250.8 MPa while maintaining acceptable elongation of 14.7%. The addition of Mo improved strength through solid solution strengthening and increased BCC phase fraction, with hardness increasing from 305.4 HV for Mo0 to 362.6 HV for Mo2. Beyond 2% Mo content, the strength and hardness decreased.","page_reference":"pages 4-5","key_passage":"Mo2 owns the highest fracture strength, 1250.8 MPa, among all the alloys. The fracture strength improves about 20 MPa, 120 MPa and 70 MPa in Mo1, Mo2, Mo3, compared with Mo0, while the elongations do not reduce significantly.","citation":"yang2019enhancing","expected_retrieval":true} | |
| {"qid":"c55c5175-664f-49e9-aed8-7c0864f7fa69","paper_id":"10.1007@s11661-019-05231-y","composition":"FeCoCrNiMn","tag":"material phases","question_type":"long_answer","question":"Was FeCoCrNiMn tested experimentally, and if so what material phases were observed during the experiments?","ground_truth_answer":"The FeCoCrNiMn alloy initially had a single-phase FCC structure. After severe cold rolling (SCR), it maintained the FCC phase with ultrafine crystalline structure and high-density dislocations. Upon annealing at 773K (500°C), σ phases with tetragonal structure formed, while maintaining the FCC matrix.","page_reference":"pages 1-4","key_passage":"The results show that the microstructure of the single-phase FCC HEA after SCR is greatly refined and mainly comprises ultrafine crystalline, high-density dislocation cell and networks... The σ phases with a tetragonal structure form upon annealing at 773 K (500 °C)","citation":"li2019effect","expected_retrieval":true} | |
| {"qid":"b1ea367e-8190-4f42-9fb6-da45d932193d","paper_id":"10.1007@s11661-019-05231-y","composition":"FeCoCrNiMn","tag":"experimental details","question_type":"long_answer","question":"What experimental processing methods were used to prepare the FeCoCrNiMn specimens?","ground_truth_answer":"The FeCoCrNiMn alloy was produced by severe cold rolling (SCR) with a 95% reduction in thickness. The initial ingot was homogenized at 1423K for 6 hours, then cold-rolled from 10mm to ~0.5mm thickness. Samples were subsequently annealed at temperatures ranging from 573K to 1373K for various durations.","page_reference":"page 2","key_passage":"An ultrafine-structured FeCoCrNiMn high-entropy alloy (HEA) was produced by severe cold rolling (SCR) with a 95 pct reduction... After being homogenized at 1423 K (1150 °C) for 6 hours, the ingot plate with an initial thickness of 10 mm was severely cold-rolled to a thickness of ~ 0.5 mm","citation":"li2019effect","expected_retrieval":true} | |
| {"qid":"90cf703a-3fe1-4c40-b1e6-f2288cea82ee","paper_id":"10.1007@s11661-019-05231-y","composition":"FeCoCrNiMn","tag":"experimental results","question_type":"long_answer","question":"What were the key findings from testing the FeCoCrNiMn alloy?","ground_truth_answer":"The severe cold rolled FeCoCrNiMn showed greatly improved hardness and strength compared to the homogenized state. The alloy began recrystallizing at 773K and was fully recrystallized at 973K after 1 hour. The material exhibited excellent thermal stability, maintaining grain size below 500nm when annealed at 923K. Samples annealed at 923K and 973K showed excellent combinations of high strength and ductility.","page_reference":"page 1","key_passage":"The SCRed HEA starts to recrystallize at an annealing temperature of 773 K (500 °C) and is fully recrystallized at 973 K (700 °C) after 1 hours... The average grain size remains below 500 nm when the SCRed HEA is annealed at 923 K (650 °C) for 1 hours... The SCRed HEAs annealed at 923 K and 973 K (650 °C and 700 °C) exhibit excellent high strength–ductility combinations","citation":"li2019effect","expected_retrieval":true} | |
| {"qid":"ee3b340f-e472-4c3c-92f3-231a2391e50f","paper_id":"10.1007@s11661-019-05231-y","composition":"Fe20Co15Cr25Ni25Al15","tag":"material phases","question_type":"long_answer","question":"Was Fe20Co15Cr25Ni25Al15 tested experimentally, and if so what phases were identified in the microstructure?","ground_truth_answer":"Insufficient information to answer - this specific composition is not discussed in the paper","page_reference":"N/A","key_passage":"Composition not found in the literature","citation":"li2019effect","expected_retrieval":false} | |
| {"qid":"36c4668c-6d6a-4818-b93c-4cc496f634c9","paper_id":"10.1007@s11661-019-05231-y","composition":"Fe20Co15Cr25Ni25Al15","tag":"experimental details","question_type":"long_answer","question":"Based on literature, how were Fe20Co15Cr25Ni25Al15 specimens prepared for experimental testing?","ground_truth_answer":"Insufficient information to answer - this specific composition is not discussed in the paper","page_reference":"N/A","key_passage":"Composition not found in the literature","citation":"li2019effect","expected_retrieval":false} | |
| {"qid":"5f99a484-59d7-4e1b-b867-5571d687a1a3","paper_id":"10.1007@s11661-019-05231-y","composition":"Fe20Co15Cr25Ni25Al15","tag":"experimental results","question_type":"long_answer","question":"For Fe20Co15Cr25Ni25Al15, what were the main experimental findings regarding mechanical properties and microstructure?","ground_truth_answer":"Insufficient information to answer - this specific composition is not discussed in the paper","page_reference":"N/A","key_passage":"Composition not found in the literature","citation":"li2019effect","expected_retrieval":false} | |
| {"qid":"519e1b56-8914-4bd9-8078-aa911eeac285","paper_id":"10.1007@s11106-019-00012-z","composition":"Ti-Cr-Fe-Ni-Cu","tag":"material phases","question_type":"long_answer","question":"Was Ti-Cr-Fe-Ni-Cu alloy tested experimentally, and if so, what phases were identified in the hot-forged and annealed samples?","ground_truth_answer":"The Ti-Cr-Fe-Ni-Cu alloy after hot forging showed mainly FCC lattice structure with few peaks of BCC phases, intermetallides and titanium. After annealing at 1200°C, the alloy contained primarily FCC phase with traces of FeCr (sigma phase), Ni3Ti, and Ti.","page_reference":"pages 534-537","key_passage":"Following grinding for 120 min and hot forging, the X-ray spectrum of the alloy is mainly represented by reflections that belong to the FCC lattice. There are few BCC phases, intermetallides, and titanium.","citation":"marych2019influence","expected_retrieval":true} | |
| {"qid":"d35f12b8-7af8-4fbc-840d-4d1be6b954b2","paper_id":"10.1007@s11106-019-00012-z","composition":"Ti-Cr-Fe-Ni-Cu","tag":"experimental details","question_type":"long_answer","question":"Based on literature, how were the Ti-Cr-Fe-Ni-Cu specimens prepared for experimental testing?","ground_truth_answer":"The Ti-Cr-Fe-Ni-Cu alloy was prepared using powder metallurgy techniques. The equiatomic powder mixture was mechanically alloyed in a planetary-ball mill for 30-120 minutes in ethyl alcohol. The powders were then compacted at 700 MPa into cylindrical billets and hot forged at 1050°C in flowing argon atmosphere. The samples were subsequently annealed at 1000, 1100, and 1200°C for 2 hours.","page_reference":"page 534","key_passage":"The powder mixture was mechanically alloyed in a planetary-ball mill with a 1 : 8 charge-to-ball weight ratio. The mill drum velocity was 800 rpm and grinding times were 30, 60, and 120 min. To avoid the oxidation and segregation of the powder particles, they were mechanically alloyed in ethyl alcohol.","citation":"marych2019influence","expected_retrieval":true} | |
| {"qid":"f437db64-c8eb-4b45-921d-66db9f6bfd18","paper_id":"10.1007@s11106-019-00012-z","composition":"Ti-Cr-Fe-Ni-Cu","tag":"experimental results","question_type":"long_answer","question":"What were the main findings from testing the Ti-Cr-Fe-Ni-Cu alloy samples?","ground_truth_answer":"The key findings showed that mechanical alloying and hot forging produced a homogeneous alloy with mainly FCC structure. The hardness increased with grinding time for both unannealed and annealed samples. Annealing at higher temperatures decreased hardness, with samples ground for 120 minutes showing maximum hardness decrease due to greater initial lattice imperfection. The microstructure became finer and more homogeneous with increased grinding time.","page_reference":"pages 538-540","key_passage":"Annealing of the hot-forged samples with increasing temperature decreases their hardness. The materials from the mixtures subjected to preliminary mechanical alloying in a planetary-ball mill show much higher hardness. The hardness increases with grinding time for both unannealed samples and those annealed at all temperatures concerned.","citation":"marych2019influence","expected_retrieval":true} | |
| {"qid":"ab54d0f0-73c2-4d9c-a74c-e95ff2783ce3","paper_id":"10.1007@s11106-019-00012-z","composition":"Ti20Cr20Fe25Ni20Cu15","tag":"material phases","question_type":"long_answer","question":"Was Ti20Cr20Fe25Ni20Cu15 tested experimentally, and if so, which material phases were identified during characterization?","ground_truth_answer":"Insufficient information to answer - this specific composition is not mentioned in the literature","page_reference":"N/A","key_passage":"Composition not found in the literature","citation":"marych2019influence","expected_retrieval":false} | |
| {"qid":"f8211b6c-a8e9-4a13-9c99-cdb2512c7ffb","paper_id":"10.1007@s11106-019-00012-z","composition":"Ti20Cr20Fe25Ni20Cu15","tag":"experimental details","question_type":"long_answer","question":"Based on literature, how were Ti20Cr20Fe25Ni20Cu15 specimens prepared for experimental analysis?","ground_truth_answer":"Insufficient information to answer - this specific composition is not mentioned in the literature","page_reference":"N/A","key_passage":"Composition not found in the literature","citation":"marych2019influence","expected_retrieval":false} | |
| {"qid":"5e5b9dae-943a-47fd-88cd-36fedfc70739","paper_id":"10.1007@s11106-019-00012-z","composition":"Ti20Cr20Fe25Ni20Cu15","tag":"experimental results","question_type":"long_answer","question":"For Ti20Cr20Fe25Ni20Cu15, what were the main experimental findings regarding its mechanical properties and microstructure?","ground_truth_answer":"Insufficient information to answer - this specific composition is not mentioned in the literature","page_reference":"N/A","key_passage":"Composition not found in the literature","citation":"marych2019influence","expected_retrieval":false} | |
| {"qid":"4aea6cde-7bf2-4f71-8e6a-c944df85b349","paper_id":"10.1002@adma.201701678","composition":"Ta1HfZrTi","tag":"material phases","question_type":"long_answer","question":"Was Ta1HfZrTi tested experimentally, and if so what phases were observed?","ground_truth_answer":"Ta1HfZrTi exhibited a single bcc phase structure with only bcc diffraction peaks observed in XRD analysis. The microstructure showed grain sizes around 100 μm.","page_reference":"1-2","key_passage":"A single bcc phase structure was obtained in the quaternary equiatomic Ta1 HEA with only bcc diffraction peaks on its XRD trace.","citation":"huang2017phase","expected_retrieval":true} | |
| {"qid":"7048282a-bcab-4cbd-9925-bb5cf52c8025","paper_id":"10.1002@adma.201701678","composition":"Ta1HfZrTi","tag":"experimental details","question_type":"long_answer","question":"How were the Ta1HfZrTi specimens prepared for experimental testing?","ground_truth_answer":"Ta1HfZrTi ingots were prepared by arc-melting pure metals (>99.9% purity) in Ti-gettered argon atmosphere, remelted 5 times, and drop-cast into 10x10x60mm copper molds. Dog-bone tensile specimens were cut by electrical discharge machining with 1.5mm thickness, 15mm gauge length and 5mm width.","page_reference":"6","key_passage":"Alloy ingots with a nominal composition of TaxHfZrTi (x is from 0 to 1) were prepared by arc-melting a mixture of pure metals with purity over 99.9 at% in a Ti-gettered argon atmosphere. All ingots were remelted at least five times to eliminate chemical imhomogeneity, and eventually drop-cast into a 10 mm × 10 mm × 60 mm copper mold. Dog-bone-shaped specimens with a thickness of 1.5 mm for tensile tests were cut from the rods by electrical discharge machining. The gauge length and width of the tensile samples are 15 and 5 mm, respectively.","citation":"huang2017phase","expected_retrieval":true} | |
| {"qid":"8a7685e8-77a9-4c98-9314-c5c090175f4b","paper_id":"10.1002@adma.201701678","composition":"Ta1HfZrTi","tag":"experimental results","question_type":"long_answer","question":"What were the key mechanical testing results for Ta1HfZrTi?","ground_truth_answer":"Ta1HfZrTi showed high strength around 1500 MPa but very limited plasticity of only 4%. The strain-hardening rate showed a sharp decrease due to quick failure after the elastic stage. The fracture surface exhibited typical brittle fracture characteristics with deformation mainly at grain boundaries.","page_reference":"2-4","key_passage":"Ta1 (#1) shows high strength (≈1500 MPa) but very limited plasticity (≈4%). Alloy Ta1 (#1) shows a sharp decrease in the strain-hardening rate for its quick failure after elastic stage.","citation":"huang2017phase","expected_retrieval":true} | |
| {"qid":"72ff3e11-fffb-4f38-9f76-0f2d29318157","paper_id":"10.1007@s11661-018-4646-8","composition":"HfNbTaTiZr","tag":"material phases","question_type":"long_answer","question":"Was HfNbTaTiZr tested experimentally, and if so what material phases were observed during the experiments?","ground_truth_answer":"HfNbTaTiZr exhibited a single-phase BCC crystal structure in the as-cast condition and after cold rolling and annealing above 1000°C. During annealing at 800°C, precipitation of Nb and Ta rich BCC2 particles occurred inside a Hf-and-Zr-enriched BCC1 matrix. The second phase particles nucleated heterogeneously inside deformation bands and slip lines.","page_reference":"1-2","key_passage":"The cold-worked material retained a single-phase microstructure and had a room temperature tensile yield stress r0.2 = 1438 MPa, peak true stress rp = 1495 MPa, and true fracture strain ef = 5 pct. Annealing at 800 C for up to 256 hours resulted in the precipitation of Nb and Ta rich particles with a BCC crystal structure inside a Hf-and-Zr-enriched BCC matrix. The second phase particles nucleated heterogeneously inside deformation bands and slip lines and coarsened during annealing.","citation":"senkov2018effect","expected_retrieval":true} | |
| {"qid":"a1908468-8d9a-49bd-a038-2b0f981ddb83","paper_id":"10.1007@s11661-018-4646-8","composition":"HfNbTaTiZr","tag":"experimental details","question_type":"long_answer","question":"What experimental preparation methods were used to process the HfNbTaTiZr alloy samples?","ground_truth_answer":"The equiatomic HfNbTaTiZr alloy was prepared by non-consumable vacuum arc melting, followed by hot isostatic pressing at 1200°C for 2 hours under argon at 207 MPa. The material was cold worked to 89% total thickness reduction through upset forging (54.5% reduction) followed by rolling (75.8% reduction). Samples were then annealed at temperatures between 800-1200°C for various times.","page_reference":"2","key_passage":"The equiatomic HfNbTaTiZr alloy was prepared by non-consumable vacuum arc (button) melting. After solidification, the button was wrapped in Ta foil and hot isostatically pressed (HIP'd) for 2 hours at 1200 C under high-purity argon using a pressure of 207 MPa. Two rectangular blocks were extracted and initially cold forged followed by rolling along the 31.3-mm direction resulting in a total thickness reduction of 89 pct.","citation":"senkov2018effect","expected_retrieval":true} | |
| {"qid":"482e7c8d-b825-45d4-baa8-279896aa4065","paper_id":"10.1007@s11661-018-4646-8","composition":"HfNbTaTiZr","tag":"experimental results","question_type":"long_answer","question":"What were the main experimental findings regarding the mechanical properties of HfNbTaTiZr?","ground_truth_answer":"The cold-worked HfNbTaTiZr had a yield stress of 1438 MPa, peak stress of 1495 MPa, and fracture strain of 5%. After annealing at 800°C, the yield and peak stresses decreased to 1071-1159 MPa and 1074-1174 MPa respectively, with fracture strains of 5-8%. Annealing at 1100°C resulted in yield stress of 1110-1115 MPa, peak stress of 1160-1195 MPa, and improved fracture strains of 12-19%.","page_reference":"1","key_passage":"The cold-worked material retained a single-phase microstructure and had a room temperature tensile yield stress r0.2 = 1438 MPa, peak true stress rp = 1495 MPa, and true fracture strain ef = 5 pct. In the two-phase material, r0.2 and rp decreased from 1159 to 1071 MPa and from 1174 to 1074 MPa, respectively, with an increase in particle diameter from 0.18 to 0.72 lm, while ef remained between 5 and 8 pct. After heat treatment at this temperature, the alloy was characterized by a single-phase BCC structure with r0.2 = 1110 to 1115 MPa, rp = 1160 to 1195 MPa, and ef = 12 to 19 pct with the maximum values attained after annealing for 1 hour.","citation":"senkov2018effect","expected_retrieval":true} | |
| {"qid":"335d3a26-6ad2-4e36-b28c-2b4dab51232b","paper_id":"10.1007@s10853-019-03567-9","composition":"NbTaWMoTi0.5Zr0.3","tag":"material phases","question_type":"long_answer","question":"Was NbTaWMoTi0.5Zr0.3 alloy experimentally investigated, and if so, what phases were identified in its microstructure?","ground_truth_answer":"Insufficient information to answer","page_reference":"N/A","key_passage":"Composition not found in the literature","citation":"guo2019correction","expected_retrieval":false} | |
| {"qid":"2f3dcc26-efb0-4a8b-af64-441ea4d3dbd8","paper_id":"10.1007@s10853-019-03567-9","composition":"NbTaWMoTi0.5Zr0.3","tag":"experimental details","question_type":"long_answer","question":"For NbTaWMoTi0.5Zr0.3, what experimental methods were used to prepare and characterize the specimens?","ground_truth_answer":"Insufficient information to answer","page_reference":"N/A","key_passage":"Composition not found in the literature","citation":"guo2019correction","expected_retrieval":false} | |
| {"qid":"eb7b40bb-db58-4522-813a-69d8fa4fca0b","paper_id":"10.1007@s10853-019-03567-9","composition":"NbTaWMoTi0.5Zr0.3","tag":"experimental results","question_type":"long_answer","question":"Based on literature, has NbTaWMoTi0.5Zr0.3 been tested, and if so, what were the main findings regarding its mechanical properties?","ground_truth_answer":"Insufficient information to answer","page_reference":"N/A","key_passage":"Composition not found in the literature","citation":"guo2019correction","expected_retrieval":false} | |
| {"qid":"b816a4cf-f6de-4d16-816c-8757006b3e32","paper_id":"10.1002@adem.200300567","composition":"CuCoNiCrAlFe","tag":"material phases","question_type":"long_answer","question":"Was CuCoNiCrAlFe alloy tested experimentally, and if so what phases were identified during characterization?","ground_truth_answer":"The CuCoNiCrAlFe alloy was experimentally tested and showed both FCC and BCC phases. XRD analysis revealed that as aluminum content (x) increased from 0 to 0.5, a simple FCC structure was observed, while at x > 0.8, a BCC structure appeared in addition to FCC. A spinodal decomposition occurred at higher Al content leading to a modulated structure composed of ordered and disordered phases.","page_reference":"2","key_passage":"Those alloys with aluminum contents from x = 0 to x = 0.5 showed a simple fcc structure. As x exceeded 0.8, a bcc structure appeared in addition to the fcc, and a spinodal decomposition occurred further on, leading to a modulated structure composed of ordered (B2) and disordered (A2) bcc phases","citation":"yeh2004novel","expected_retrieval":true} | |
| {"qid":"79af6d1f-0e1f-4255-87cc-6d92320b511a","paper_id":"10.1002@adem.200300567","composition":"CuCoNiCrAlFe","tag":"experimental details","question_type":"long_answer","question":"How were the experimental CuCoNiCrAlFe specimens prepared for testing and characterization?","ground_truth_answer":"The alloys were prepared by arc-melting the constituent elements at 500 A in a cold copper hearth. The ingots were approximately 50 mm in diameter and 20 mm thick. Multiple remelting cycles were performed to improve homogeneity. Specimens were re-melted and splat-quenched at cooling rates of 10^6 K/s. Some specimens were also machined into 5 mm thick plates for sputtering targets. Thin films were deposited on silicon substrates by RF sputtering.","page_reference":"4-5","key_passage":"The multiple principal element HE alloys in this study were prepared by arc-melting the constituent elements at a current of 500 A in a cold copper hearth. The solidified ingots were approximately 50 mm in diameter and 20 mm thick. Melting and casting were performed at a pressure of 0.01 atm after purging with argon three times. Repeated melting for at least five cycles was carried out to improve chemical homogeneity of the alloy.","citation":"yeh2004novel","expected_retrieval":true} | |
| {"qid":"17f9ad89-bdae-48d0-a42d-8ec49fb3d3b2","paper_id":"10.1002@adem.200300567","composition":"CuCoNiCrAlFe","tag":"experimental results","question_type":"long_answer","question":"What were the key findings from testing the CuCoNiCrAlFe alloy system?","ground_truth_answer":"The CuCoNiCrAlFe alloy system showed excellent stability and mechanical properties. The alloy exhibited hardness values from 130 to 1100 Hv depending on composition. It demonstrated good wear resistance similar to ferrous alloys and excellent oxidation resistance up to 1100°C. The alloy also showed good corrosion resistance and could be processed into both bulk and thin film forms with nanocrystalline structures.","page_reference":"3-4","key_passage":"It was also found that the wear resistance of HE alloys was similar to that of ferrous alloys of the same hardness. Furthermore, many of the HE alloys, especially those containing Cu, Ti, Cr, Ni, or Co, exhibited corrosion resistance as good as stainless steels, and the HE alloys containing Cr or Al demonstrated an excellent oxidation resistance, up to 1100 °C.","citation":"yeh2004novel","expected_retrieval":true} | |
| {"qid":"f55e39d2-c2ab-4a44-8a87-247b3cc0ac6c","paper_id":"10.1002@adem.200300567","composition":"Ti25Nb25Zr25Ta15Mo10","tag":"material phases","question_type":"long_answer","question":"Was Ti25Nb25Zr25Ta15Mo10 tested experimentally, and if so, which material phases were identified during characterization?","ground_truth_answer":"Insufficient information to answer - this composition is not mentioned in the paper","page_reference":"N/A","key_passage":"Composition not found in the literature","citation":"yeh2004nanostructured","expected_retrieval":false} | |
| {"qid":"6a42bcc8-0060-4c3e-91d7-872878f05884","paper_id":"10.1002@adem.200300567","composition":"Ti25Nb25Zr25Ta15Mo10","tag":"experimental details","question_type":"long_answer","question":"For Ti25Nb25Zr25Ta15Mo10, what preparation methods were used to synthesize the experimental specimens?","ground_truth_answer":"Insufficient information to answer - this composition is not mentioned in the paper","page_reference":"N/A","key_passage":"Composition not found in the literature","citation":"yeh2004nanostructured","expected_retrieval":false} | |
| {"qid":"e4ed9b49-d577-4470-be60-c81fe4693583","paper_id":"10.1002@adem.200300567","composition":"Ti25Nb25Zr25Ta15Mo10","tag":"experimental results","question_type":"long_answer","question":"Based on literature, has Ti25Nb25Zr25Ta15Mo10 been tested, and if so what were the main findings regarding its properties and performance?","ground_truth_answer":"Insufficient information to answer - this composition is not mentioned in the paper","page_reference":"N/A","key_passage":"Composition not found in the literature","citation":"yeh2004nanostructured","expected_retrieval":false} | |
| {"qid":"a0e248fd-1a6c-4310-98e9-1861f8e297e6","paper_id":"10.1007@s00339-019-2484-1.pdf","composition":"TiZrHf","tag":"experimental details","question_type":"long_answer","question":"Was the TiZrHf composition tested experimentally, and if so, what specific preparation methods were employed for the experimental specimens?","ground_truth_answer":"The TiZrHf alloy was experimentally tested. Its specimens were prepared by vacuum arc melting, followed by remelting at least six times for homogenization. The material was then solidified in a water-cooled copper hearth. The vacuum chamber was evacuated to 3 × 10−3 Pa and backfilled to 0.05 Pa with high-purity Ar gas.","page_reference":"4","key_passage":"The purity of the raw materials (Ti, Zr, Hf, Sc, and Y) was more than 99.99 wt.%. All the alloys were melted by vacuum arc melting, remelted at least six times for homogenization, and solidified in a water-cooled copper hearth. Then, the vacuum chamber was evacuated to 3 × 10−3 Pa and backfilled to 0.05 Pa with high-purity Ar gas.","citation":"Huang2019Effect","expected_retrieval":true} | |
| {"qid":"c9172a1f-8d62-4a81-8674-d273ab00b1b9","paper_id":"10.1007@s00339-019-2484-1.pdf","composition":"TiZrHf","tag":"material phases","question_type":"long_answer","question":"If the TiZrHf alloy was investigated, which material phases were identified during the experiments?","ground_truth_answer":"The TiZrHf alloy was investigated and exhibited a typical single-HCP phase structure. The lattice constants for this phase were determined to be a = 3.1624 Å, c = 4.9967 Å, and c/a = 1.58. All four RHEAs, including TiZrHf, showed an HCP-based structure because their constituent elements shared similar structures and characteristics.","page_reference":"1, 5","key_passage":"All the four RHEAs showed a hexagonal close-packed (HCP)-based structure. [1] Figure 1 shows the XRD patterns of TiZrHf, TiZrHfSc, TiZrHfY, and TiZrHfScY alloys. TiZrHf alloy exhibited a typical single-HCP phase structure. The values of the lattice constants of TiZrHf alloy were a = 3.1624 Å, c = 4.9967 Å, and c/a = 1.58. ... The HCP-structured TiZrHf, TiZrHfSc, TiZrHfY, and TiZrHf-ScY alloys formed because all the composition elements had the same structure and similar characteristics inherited by TiZrHf, TiZrHfSc, TiZrHfY, and TiZrHfScY alloys.","citation":"Huang2019Effect","expected_retrieval":true} | |
| {"qid":"854ca88e-5afa-4616-9275-6d066398bdee","paper_id":"10.1007@s00339-019-2484-1.pdf","composition":"TiZrHf","tag":"experimental results","question_type":"long_answer","question":"What were the main findings obtained from testing the TiZrHf alloy?","ground_truth_answer":"The TiZrHf alloy showed a hardness of 211 HV, yield strength of 773 MPa, fracture strength of 1184 MPa, and ductility of 17.0%. Its electrical conductivity was 1.82 %ICAS, which was lower than pure metals but comparable in resistivity (0.96 × 10−6 Ω m2/m) to traditional electrical resistance alloys. The alloy exhibited a typical paramagnetic behavior.","page_reference":"1, 8, 9, 10, 11, 12, 14, 15","key_passage":"All the four alloys showed a typical paramagnetic behavior. [1] Table 2 and Fig. 3 show the mechanical properties of TiZ-rHf, TiZrHfSc, TiZrHfY, and TiZrHfScY alloys. ... Alloy TiZrHf Hardness (HV) 211 Yield strength (MPa) 773 Fracture strength (MPa) 1184 Ductility (%) 17.0 [2] Table 3 shows the conductivity of TiZrHf, TiZrHfSc, TiZrHfY, and TiZrHfScY alloys and their component ele-ments. The conductivity of TiZrHf, TiZrHfSc, TiZrHfY, and TiZrHfScY alloys was found to be lower than that of the pure metals. This was because the HEAs with serious lat-tice distortion led to electron scattering and decreased the conductivity. [3] ... Alloy Conductiv-ity (%ICAS) TiZrHf 1.82 [4] Table 4 shows the resistivity of TiZrHf, TiZrHfSc, TiZ-rHfY, and TiZrHfScY alloys and some common electrical resistance alloys at room temperature. It shows that the resistivity of TiZrHf, TiZrHfSc, TiZrHfY, and TiZrHfScY alloys was comparable to that of traditional electrical resis-tivity alloys at room temperature, making TiZrHf, TiZrHfSc, TiZrHfY, and TiZrHfScY alloys suitable for applications as electrical resistance alloys. [5] Figure 4 shows the magnetization curves of TiZrHf, TiZrHfSc, TiZrHfY, and TiZrHfScY alloys. All the alloys exhibited a typical paramagnetic behavior. [6]","citation":"Huang2019Effect","expected_retrieval":true} | |
| {"qid":"6a1e3f10-6acc-4f5b-8ea0-834f28524aa2","paper_id":"10.1007@s00339-019-2484-1.pdf","composition":"TiZrHfSc","tag":"experimental details","question_type":"long_answer","question":"Has the TiZrHfSc composition been experimentally evaluated, and if so, how were its specimens prepared for evaluation?","ground_truth_answer":"The TiZrHfSc alloy was experimentally evaluated. Its preparation involved vacuum arc melting, followed by remelting at least six times to ensure homogenization. The melted alloy was then solidified in a water-cooled copper hearth. The process was conducted under an evacuated chamber (3 × 10−3 Pa) backfilled with high-purity Ar gas (0.05 Pa).","page_reference":"4","key_passage":"The purity of the raw materials (Ti, Zr, Hf, Sc, and Y) was more than 99.99 wt.%. All the alloys were melted by vacuum arc melting, remelted at least six times for homogenization, and solidified in a water-cooled copper hearth. Then, the vacuum chamber was evacuated to 3 × 10−3 Pa and backfilled to 0.05 Pa with high-purity Ar gas.","citation":"Huang2019Effect","expected_retrieval":true} | |
| {"qid":"5f6907b2-cb30-4846-8983-1d727fc9bfe7","paper_id":"10.1007@s00339-019-2484-1.pdf","composition":"TiZrHfSc","tag":"material phases","question_type":"long_answer","question":"Based on literature, was the TiZrHfSc composition analyzed experimentally, and if so, which material phases were found during the analysis?","ground_truth_answer":"The TiZrHfSc alloy was analyzed experimentally and comprised dual HCP phases (HCP1 + HCP2). The addition of Sc element led to this dual solution structure. The HCP1 phase had lattice constants a = 3.1976 Å, c = 5.0455 Å, and c/a = 1.58, while HCP2 had a = 3.0849 Å, c = 4.7979 Å, and c/a = 1.56. SEM images revealed a needle-like dual-phase structure, with HCP1 being near-equiatomic and HCP2 rich in Sc and Ti.","page_reference":"1, 5, 6","key_passage":"All the four RHEAs showed a hexagonal close-packed (HCP)-based structure. [1] After the addition of elements Sc and Y, the diffraction peaks shifted to a lower 2θ degree because Sc and Y elements had larger atomic radii causing lattice expansion... The TiZrHfSc alloy comprised dual HCP (HCP1 + HCP2) phases. The addition of Sc element led the formation of dual solution structure. The values of the lattice constants of TiZrHfSc alloy were a = 3.1976 Å, c = 5.0455 Å, and c/a = 1.58, and a = 3.0849 Å, c = 4.7979 Å, and c/a = 1.56 for HCP1 and HCP2 phases, respectively. [7] The TiZrHfSc alloy exhib-ited a needle-like dual-phase structure. The composition (Table 1) of the needle-like phase (denoted by HCP1) was near-equiatomic with slightly less amount of Sc element, and the phase between the HCP1 phase (denoted by HCP2) was rich in Sc and Ti. The volume fraction of the two phases was about 93% and 7% for HCP1 and HCP2 phases, respectively. [8]","citation":"Huang2019Effect","expected_retrieval":true} | |
| {"qid":"53156616-c924-4ea3-8296-11b58093d8f7","paper_id":"10.1007@s00339-019-2484-1.pdf","composition":"TiZrHfSc","tag":"experimental results","question_type":"long_answer","question":"What overall results were observed from testing the TiZrHfSc alloy?","ground_truth_answer":"The TiZrHfSc alloy exhibited improved mechanical properties with a hardness of 233 HV, yield strength of 1001 MPa, fracture strength of 1800 MPa, and ductility of 21.9%, attributed to its fine lamellar dual HCP structure. Its electrical conductivity was the lowest among the tested alloys at 1.32 %ICAS, correlating with a high resistivity of 1.33 × 10−6 Ω m2/m, suitable for electrical resistance applications. The alloy also showed typical paramagnetic behavior.","page_reference":"1, 8, 9, 10, 11, 12, 14, 15","key_passage":"Both the strength and ductility increased in the TiZrHfSc alloy compared with the TiZrHf alloy because of the addition of Sc element and the formation of a fine needle-like lamellar structure in the former. [1] The addition of elements Sc and Y led to the increase in hardness, which should be attributed to the solid solution strengthen-ing effect and grain refinement. The TiZrHfSc alloy exhib-ited the best mechanical properties among all the four alloys. This might be related to the fine lamellar structure consist-ing of alternating dual HCP phases. [9] Table 2 ... Alloy TiZrHfSc Hardness (HV) 233 Yield strength (MPa) 1001 Fracture strength (MPa) 1800 Ductility (%) 21.9 [2] The conductivity of TiZrHf, TiZrHfSc, TiZrHfY, and TiZrHfScY alloys was found to be lower than that of the pure metals. [3] Among the alloys, the TiZrHfSc alloy has the lowest electrical conductivity, because reducing the average grain size reduces the electrical conductivity and increases the resistivity. [5] Table 3 ... Alloy Conductiv-ity (%ICAS) TiZrHfSc 1.32 [4] Table 4 ... Alloy Resistivity (10−6 Ω m2/m) TiZrHfSc 1.33 [4] All the alloys exhibited a typical paramagnetic behavior. [6]","citation":"Huang2019Effect","expected_retrieval":true} | |
| {"qid":"dbac8723-3bdf-4b55-ad05-a378694a4b05","paper_id":"10.1007@s00339-019-2484-1.pdf","composition":"TiZrHfY","tag":"experimental details","question_type":"long_answer","question":"For the TiZrHfY alloy, was it subjected to experimental testing, and if so, what preparation steps were taken for its specimens?","ground_truth_answer":"The TiZrHfY alloy was subjected to experimental testing. Its specimens were prepared using vacuum arc melting. Following melting, the alloys were remelted a minimum of six times for proper homogenization. Solidification occurred in a water-cooled copper hearth. The preparation environment involved evacuating the vacuum chamber to 3 × 10−3 Pa and then backfilling it to 0.05 Pa with high-purity Ar gas.","page_reference":"4","key_passage":"The purity of the raw materials (Ti, Zr, Hf, Sc, and Y) was more than 99.99 wt.%. All the alloys were melted by vacuum arc melting, remelted at least six times for homogenization, and solidified in a water-cooled copper hearth. Then, the vacuum chamber was evacuated to 3 × 10−3 Pa and backfilled to 0.05 Pa with high-purity Ar gas.","citation":"Huang2019Effect","expected_retrieval":true} | |
| {"qid":"a811bd01-e08b-41d5-82b7-75b1d2ebfa3d","paper_id":"10.1007@s00339-019-2484-1.pdf","composition":"TiZrHfY","tag":"material phases","question_type":"long_answer","question":"Did experimental analysis of the TiZrHfY alloy reveal its material phases, and if so, what were they?","ground_truth_answer":"Experimental analysis of the TiZrHfY alloy revealed it mainly comprised an HCP phase and a small number of electride phase, identified as α(Y) with a space group of P63/mmc. The addition of Y element led to the observation of this electride phase. The HCP phase lattice constants were nearly identical to the HCP1 phase in TiZrHfSc, while the α(Y) electride phase had a = 3.6471 Å, c = 5.7285 Å, and c/a = 1.57. SEM images showed a dendrite structure with Y-rich electride in the interdendrite section.","page_reference":"1, 5, 6","key_passage":"All the four RHEAs showed a hexagonal close-packed (HCP)-based structure. [1] An electride phase with a struc-ture of α(Y) (space group of P63/mmc) was observed with the addition of element Y. The TiZrHfY alloy mainly com-prised an HCP phase and a small number of electride phase. The values of lattice constants of the HCP phase in the TiZ-rHfY alloy were almost the same as those of the HCP1 phase in the TiZrHfSc alloy, and the values of lattice constants of the α(Y) electride phase were a = 3.6471 Å, c = 5.7285 Å, and c/a = 1.57. [7] The TiZrHfY alloy exhib-ited a dendrite structure, with the interdendrite section being Y-rich (over 90 at%) electride phase (denoted by E). This was because the chemical mixing enthalpies between Y and other elements were higher than those of other atom pairs. Furthermore, the radius of the Y element was much larger than those of Ti, Zr, and Hf elements. Thus, only a small amount of Y (15.79 at.%) melted into the matrix phase, and the electride phase contained more than 90 at.% of Y. The volume fraction of the two phases was about 84.8% and 15.2% for the matrix and electride phases, respectively. [8]","citation":"Huang2019Effect","expected_retrieval":true} | |
| {"qid":"b2e16503-03d0-43df-a66f-1a54dca250bc","paper_id":"10.1007@s00339-019-2484-1.pdf","composition":"TiZrHfY","tag":"experimental results","question_type":"long_answer","question":"What notable results were derived from the experimental investigation of the TiZrHfY alloy?","ground_truth_answer":"The experimental investigation showed that the mechanical properties of TiZrHfY alloy decreased due to Y segregation and the formation of a hard electride phase at grain boundaries, with a hardness of 241 HV, yield strength of 554 MPa, fracture strength of 1071 MPa, and ductility of 17.7%. Its electrical conductivity was the highest among the alloys at 1.98 %ICAS, attributed to its large grain size and conductive electride phase, with a resistivity of 0.88 × 10−6 Ω m2/m. The alloy also displayed paramagnetic behavior.","page_reference":"1, 8, 9, 10, 11, 12, 14, 15","key_passage":"The mechanical properties of TiZrHfY and TiZrHfScY alloys decreased after the addition of Y element because of the segregation. [1] After adding element Y, the hard electride phase formed at the grain boundary, which decreased the strength and ductility of TiZrHfY and TiZrHfScY alloys. [9] Table 2 ... Alloy TiZrHfY Hardness (HV) 241 Yield strength (MPa) 554 Fracture strength (MPa) 1071 Ductility (%) 17.7 [2] The conductivity of TiZrHf, TiZrHfSc, TiZrHfY, and TiZrHfScY alloys was found to be lower than that of the pure metals. [3] Similarly, the TiZrHfY alloy showed the highest electrical conductivity because the TiZrHfY alloy had a large grain size and electride phase with high conductivity. [5] Table 3 ... Alloy Conductiv-ity (%ICAS) TiZrHfY 1.98 [4] Table 4 ... Alloy Resistivity (10−6 Ω m2/m) TiZrHfY 0.88 [4] All the alloys exhibited a typical paramagnetic behavior. [6]","citation":"Huang2019Effect","expected_retrieval":true} | |
| {"qid":"4d479c12-6f77-41de-adb8-728f3cf57e1d","paper_id":"10.1007@s00339-019-2484-1.pdf","composition":"TiZrHfScY","tag":"experimental details","question_type":"long_answer","question":"If the TiZrHfScY composition was experimentally tested, what method was used to prepare the experimental specimens?","ground_truth_answer":"The TiZrHfScY alloy was experimentally tested. Its specimens were prepared by vacuum arc melting and then remelted at least six times to ensure homogenization. Solidification occurred in a water-cooled copper hearth. The experimental setup involved evacuating the vacuum chamber to 3 × 10−3 Pa and subsequently backfilling it with high-purity Ar gas to 0.05 Pa.","page_reference":"4","key_passage":"The purity of the raw materials (Ti, Zr, Hf, Sc, and Y) was more than 99.99 wt.%. All the alloys were melted by vacuum arc melting, remelted at least six times for homogenization, and solidified in a water-cooled copper hearth. Then, the vacuum chamber was evacuated to 3 × 10−3 Pa and backfilled to 0.05 Pa with high-purity Ar gas.","citation":"Huang2019Effect","expected_retrieval":true} | |
| {"qid":"f492e29b-c623-44c7-b4b7-2eac4dc13103","paper_id":"10.1007@s00339-019-2484-1.pdf","composition":"TiZrHfScY","tag":"material phases","question_type":"long_answer","question":"Which material phases were observed during experiments on the TiZrHfScY alloy?","ground_truth_answer":"During experiments, the TiZrHfScY alloy mainly comprised dual HCP phases and a small number of αin(Y) electride phase. The lattice constants for the two HCP phases were almost identical to those found in the TiZrHfSc alloy, while the electride phase's lattice constants were similar to those in the TiZrHfY alloy. The composition of the two HCP phases in TiZrHfScY was very close to that of the TiZrHfSc alloy, with almost no Y detected, while the electride phase contained almost no Ti, Zr, or Hf.","page_reference":"1, 5, 7","key_passage":"All the four RHEAs showed a hexagonal close-packed (HCP)-based structure. [1] The TiZrHfScY alloy mainly comprised dual HCP phases and a small number of αin(Y) electride phase. The values of lattice constants of the two HCP phases in the TiZrHfScY alloy were almost the same as those of the HCP1 and HCP2 phases in the TiZrHfSc alloy, and the values of lattice constants of the electride phase were almost the same as those of the electride phase in the TiZrHfY alloy. [7] The TiZrHfScY alloy comprised a dual HCP structure and an electride phase. The composition of the two HCP phases in TiZrHfScY was very close to that of the TiZrHfSc alloy, and almost no Y element was detected. On the contrary, almost no Ti, Zr, or Hf elements were detected in the electride phase. According to the Sc–Y binary phase diagram, Sc and Y were mutually soluble and formed an α (Y) electride phase. This phenomenon indicated a similarity in the structure of the electride phase of TiZrHfScY and TiZrHfY alloys, which matched with the results of the XRD patterns. [10]","citation":"Huang2019Effect","expected_retrieval":true} | |
| {"qid":"7d17ecb5-6677-42a5-841c-c79a0a024f4e","paper_id":"10.1007@s00339-019-2484-1.pdf","composition":"TiZrHfScY","tag":"experimental results","question_type":"long_answer","question":"What were the summarized results obtained from testing the TiZrHfScY alloy?","ground_truth_answer":"Testing revealed that the mechanical properties of TiZrHfScY alloy decreased due to Y segregation, with a hardness of 256 HV, yield strength of 793 MPa, fracture strength of 1365 MPa, and ductility of 15.7%. Its electrical conductivity was 1.42 %ICAS, which was lower than pure elements but its resistivity of 1.23 × 10−6 Ω m2/m was comparable to traditional electrical resistance alloys. The alloy also exhibited typical paramagnetic behavior.","page_reference":"1, 8, 9, 10, 11, 12, 14, 15","key_passage":"The mechanical properties of TiZrHfY and TiZrHfScY alloys decreased after the addition of Y element because of the segregation. [1] The addition of elements Sc and Y led to the increase in hardness, which should be attributed to the solid solution strengthen-ing effect and grain refinement. After adding element Y, the hard electride phase formed at the grain boundary, which decreased the strength and ductility of TiZrHfY and TiZrHfScY alloys. [9] Table 2 ... Alloy TiZrHfScY Hardness (HV) 256 Yield strength (MPa) 793 Fracture strength (MPa) 1365 Ductility (%) 15.7 [2] The conductivity of TiZrHf, TiZrHfSc, TiZrHfY, and TiZrHfScY alloys was found to be lower than that of the pure metals. [3] Table 3 ... Alloy Conductiv-ity (%ICAS) TiZrHfScY 1.42 [4] Table 4 ... Alloy Resistivity (10−6 Ω m2/m) TiZrHfScY 1.23 [4] All the alloys exhibited a typical paramagnetic behavior. [6]","citation":"Huang2019Effect","expected_retrieval":true} | |
| {"qid":"f9048823-5242-48ba-abd9-061528d23cdf","paper_id":"10.1007@s10853-018-03196-8.pdf","composition":"Ni20Co20Fe20Cr20Ga20","tag":"experimental details","question_type":"long_answer","question":"Was the Ni20Co20Fe20Cr20Ga20 composition tested experimentally, and if so, what experimental methods were employed for preparing the specimens?","ground_truth_answer":"The Ni20Co20Fe20Cr20Ga20 alloy was prepared by induction melting high-purity elements at approximately 1800 °C in a water-cooled copper mold under Ar gas, with the melting process repeated five times for homogeneity. The master alloy was then remelted and spin-cast into a wedge-shaped copper mold using centrifugal casting equipment. This preparation method allowed for investigation of different cooling rates within a single specimen, varying from approximately 10^5 K/s at the tip to 10^2 K/s at the bottom.","page_reference":"10","key_passage":"High-purity elements (99.99% delivered by Johnson Matthey company) were used to prepare the Ni20-Co20Fe20Cr20Ga20 sample having a total mass of 20 g (composition in at%). The ingot was melted at about 1800 °C in a water-cooled copper mold using induction melting. Ar gas with titanium getter was used to prevent the sample from oxidation. The melting process was repeated five times to achieve homogeneity of the sample. As the master alloy was ready, it was placed and remelted in a centrifugal casting equipment and spin-cast into a wedge-shaped copper mold. This type of mold allows us to investigate the effect of different cooling rates in a single specimen due to the varying thickness along the sample. We note here that in some earlier studies dealing with cooling rate effects of NiCoFeCr-based HEA alloys [1, 2] the different cooling rates were achieved by changing the casting method. Figure 1 shows the optical image of the investi-gated NiCoFeCrGa HEA sample. According to the empirical relation suggested by Pryds and Huang [3], the cooling rate of different (d) thickness parts of the wedge is reciprocally proportional to d2 so that the cooling rate (* 105 K/s at the tip (point A) is about three orders of magnitude higher than that (* 102 K/s at the bottom (point D).","citation":"Molnar2018Effect","expected_retrieval":true} | |
| {"qid":"06266346-66a0-4a32-b7e1-d8df5c730788","paper_id":"10.1007@s10853-018-03196-8.pdf","composition":"Ni20Co20Fe20Cr20Ga20","tag":"material phases","question_type":"long_answer","question":"Was the Ni20Co20Fe20Cr20Ga20 composition tested experimentally, and if so, which material phases were observed during the experiments and what were their characteristics?","ground_truth_answer":"Experimental testing of Ni20Co20Fe20Cr20Ga20 revealed a multiphase microstructure consisting of both face-centered cubic (FCC) and body-centered cubic (BCC) phases, forming a self-similar solidified structure. The FCC phase appeared as dendrite regions, primarily enriched in Fe, Co, and Cr. Conversely, the BCC phase formed the inter-dendrite regions, being richer in Ni and Ga. While the general phase structure remained consistent across different cooling rates, the precise composition of these individual phases varied depending on the cooling rate.","page_reference":"3","key_passage":"microstructure which has a mixture of two—FCC and BCC—phases, leading to a self-similarity of the solidified structure formed in the sample. Furthermore, the cooling rate influences both the composition of the two phase-components and the ratio of their volume fractions, determining the mechanical properties of the sample. The present results confirm the grouping of Co, Fe and Cr in the FCC phase and that of Ni and Ga in BCC phase in the NiCoFeCrGa high-entropy alloy system. An empirical rule is suggested to predict how the phase-components can be expected in this complex high-entropy alloy. ... With Ga addi-tion, the average VEC value drops down to 7.2 and in agreement with the VEC rule described before. The NiCoFeCrGa contains both BCC and FCC phases, which was confirmed by XRD and also by EBSD measurements [4]. In the present work, the ratio of these two phases and their effect on the mechanical properties are discussed. ... In all positions (from x 0 to x 17 mm) multiphase—dendritic—structure containing darker (dendrite) and brighter (inter-dendrite) regions can be observed. ... The results of the EBSD investigations show that the dendrite areas in the images mark the FCC phase and the inter-dendrite ones present the BCC phase regions. The compositions of the different phases shown in the SEM images were analyzed by EDS measurements and are given in Table 1. It can be seen that at all positions, the FCC phase—the dendrites—is more rich in Fe, Co and Cr and the BCC phase—the inter-dendrite—contains more Ni and Ga. This result is well established in our previous work [5]. ... It can be also observed that the composition of both FCC (dendrite) and BCC (inter-dendrite) regions changes along the sample due to the change in the cooling rate.","citation":"Molnar2018Effect","expected_retrieval":true} | |
| {"qid":"d49f3bc0-8366-47bb-8084-0611704b0dbe","paper_id":"10.1007@s10853-018-03196-8.pdf","composition":"Ni20Co20Fe20Cr20Ga20","tag":"experimental results","question_type":"long_answer","question":"Was the Ni20Co20Fe20Cr20Ga20 composition tested experimentally, and if so, what were the overall findings from testing the alloy regarding its mechanical properties and microstructure?","ground_truth_answer":"Experimental results on Ni20Co20Fe20Cr20Ga20 demonstrated that the cooling rate critically impacts both the developing microstructure and mechanical properties, leading to a self-similarity of the solidified structure. Higher cooling rates resulted in smaller and denser dendrite arms, while lower rates yielded larger and sparser ones. The alloy's hardness increased by approximately 25% from the tip (high cooling rate) to the bottom (low cooling rate) of the wedge-shaped sample. This hardness increase was directly correlated with a 15% rise in the volume fraction of the harder BCC phase, confirming its strengthening effect within the composite-like microstructure.","page_reference":"2","key_passage":"The effect of cooling rate on the microstructure and mechanical properties of equimolar NiCoFeCrGa high-entropy alloy was studied by scanning electron microscopy, energy-dispersive X-ray spectroscopy and electron backscatter diffraction (EBSD), as well as by microhardness tests. Experimental results show that the cooling rate has a crucial impact on the developing microstructure which has a mixture of two—FCC and BCC—phases, leading to a self-similarity of the solidified structure formed in the sample. Furthermore, the cooling rate influences both the composition of the two phase-components and the ratio of their volume fractions, determining the mechanical properties of the sample. ... The size of the local dendrite/inter-dendrite regions strongly depends on the investigated position due to the dif-ferent cooling rates along the wedge, but the phase structure remains the same. ... It is also worth mentioning that the cooling rate affects the size of the dendrites. The spacing of the dendrite arms is larger for lower cooling rates (* 102 K/s) and smaller for higher cooling rates (* 105 K/s) which means that for a given length, more and thinner dendrite arms will develop at high cooling rates, as well as less and thicker dendrite arms form at lower cooling rates. This trend is clearly visible in Fig. 2, where small and dense (* 1-lm spacing) dendrites can be observed in the A inset, while large and sparse (* 5-lm spacing) dendrites can be seen in the D inset. ... The results of hardness tests show clearly that the hardness (HV) is increasing from the tip to the bottom of the wedge, resulting in an increment of about 25% in hardness. Although the size of the components may also have an effect on the global strength, it should be emphasized that hard-ness change follows the trend of the ratio of BCC and FCC phases. The mixture of the soft and ductile FCC phase and the hard and brittle BCC component leads to a composite-like microstructure, the hardness of which is determined mainly by the volume fraction of the components. The 15% increase in the volume fraction of the BCC phase along the sample results may certainly cause a 25% increment in hardness. The obtained experimental results confirm the strengthening effect of BCC phase in this type of HEA [28–30].","citation":"Molnar2018Effect","expected_retrieval":true} | |
| {"qid":"a444143f-e275-4b3f-b852-374888764c65","paper_id":"10.1002@adem.200900171.pdf","composition":"AlCo1.5CrFeMo0.5Ni","tag":"material phases","question_type":"long_answer","question":"Was AlCo1.5CrFeMo0.5Ni experimentally tested, and what crystal structures or material phases were identified in this composition?","ground_truth_answer":"AlCo1.5CrFeMo0.5Ni was experimentally tested. This alloy (Co-1.5) was found to have BCC and s phases in its as-cast state. Like Co-1.0, its microstructure was characterized by a simple dendritic structure, with both dendrite and interdendrite exhibiting a modulated structure.","page_reference":"1, 11, 15, 21, 42","key_passage":"As cobalt content increases, the microstructure changes from dendrite to polygrain type and the constituent phases change from BCCþ s at x¼ 0.5 to BCCþ FCCþ s at x¼ 2.0 [1]. Table 1 shows the designated compositions of experimental AlCoxCrFeMo0.5Ni alloys (Co-x alloy hereafter represent the alloy with cobalt content x) [2]. Only three crystal structures: FCC (a¼ 3.60 Å), BCC (a¼ 2.87 Å) with a small ordered peak at around 318, and s phase (a¼ 8.94 Å and c¼ 4.65 Å) are identified [2]. The Co-0.5, Co-1.0, and Co-1.5 alloys are characterized as having BCC and s phases [3]. The Co-1.0 andCo-1.5 alloys contain no eutectic regions but exhibit a simple dendritic structure composing of dendrite (labeled as A) and interdendrite (labeled as B) [19]. With the increased content of Co, an FCC stabilizer, the crystal structure of AlCoxCrFeMo0.5Ni HEAs gradually changes from BCCþ s phase at x¼ 0.5 to BCCþ FCCþ s phase at x¼ 2.0 [7].","expected_retrieval":true} | |
| {"qid":"787e5956-6f15-423c-8df2-5825dcbbc648","paper_id":"10.1002@adem.200900171.pdf","composition":"AlCo1.5CrFeMo0.5Ni","tag":"experimental details","question_type":"long_answer","question":"If AlCo1.5CrFeMo0.5Ni was tested, what preparation methods were used for the experimental specimens of AlCo1.5CrFeMo0.5Ni?","ground_truth_answer":"AlCo1.5CrFeMo0.5Ni was tested experimentally. Specimens were prepared via arc-melting of high-purity raw elemental materials (Al, Co, Cr, Fe, Ni) and a Fe-61.5wt% Mo master alloy under a protective argon atmosphere. To ensure compositional uniformity, each sample was re-melted and re-solidified four times. Hot hardness specimens, 1.5 mm thick and 10 mm in diameter, were prepared by standard metallographic grinding and polishing, finishing with 1mm grade diamond paste.","page_reference":"7, 8, 10","key_passage":"Raw elemental material, Al, Co, Cr, Fe, and Ni with purity higher than 99.5wt% and master alloy, Fe-61.5wt% Mo, all in granular shape were melted to prepare the alloys by using arc-melting method under a protective atmosphere of argon [8]. Four times of re-melting and re-solidification were performed for each sample to assure the uniform composition [9]. The specimens for hot hardness measurements were 1.5 mm in thickness and 10 mm in diameter [10]. They were ground and polished by standard metallographic procedure. Final polish was done with diamond paste of 1mm grade [10].","expected_retrieval":true} | |
| {"qid":"62d4fc9f-0164-4bf3-9d4a-b8a5d5b479ce","paper_id":"10.1002@adem.200900171.pdf","composition":"AlCo1.5CrFeMo0.5Ni","tag":"experimental results","question_type":"long_answer","question":"Based on the literature, was AlCo1.5CrFeMo0.5Ni tested experimentally, and what overall results were obtained from the AlCo1.5CrFeMo0.5Ni alloy?","ground_truth_answer":"AlCo1.5CrFeMo0.5Ni was experimentally tested. Its room temperature Vickers hardness was Hv 711. As Co content increased to 1.5, the volume fraction of s phase decreased, leading to a reduction in hardness compared to lower Co content alloys. While it maintained a high hardness level, its softening coefficient (BII) above the transition temperature (988K) became more negative than Co-0.5 and Co-1.0 alloys, indicating that its hardness declined faster at elevated temperatures.","page_reference":"1, 28, 35, 36, 43","key_passage":"The alloy hardness varies fromHv 788 at x¼ 0.5 to Hv 596 at x¼ 2.0 [1]. As Co content increases, the alloy hardness decreases due to the decreased amount of s phase [11]. For the variation of hardness shown in Figure 3(a), it relates with the relative volume fractions of hard s phase, medium hard BCC phase, and soft FCC phase [21]. The alloy hardness decreases with decreased volume fraction of s phase as the Co content increases from x¼ 0.5 to x¼ 1.5 [21]. A great hardness decrease occurs from Hv 711 at x¼ 1.5 to Hv 596 at x¼ 2.0 [14]. The values of transition temperature (TT), intrinsic hardness (A), and softening coefficient (B) calculated according to Westbrook are summarized in Table 3 [17]. However, the slope (BII) above transition temperature of Co-1.5 alloy becomes more negative than those of Co-0.5 and Co-1.0 alloys, indicating that the hardness of Co-1.5 alloy declines faster than Co-0.5 and Co-1.0 [22].","expected_retrieval":true} | |
| {"qid":"8c325f9f-b699-407e-a2e0-876490851afa","paper_id":"10.1002@adem.200900171.pdf","composition":"AlCo2.0CrFeMo0.5Ni","tag":"material phases","question_type":"long_answer","question":"Was AlCo2.0CrFeMo0.5Ni tested experimentally, and if so, which material phases were observed during experiments for AlCo2.0CrFeMo0.5Ni?","ground_truth_answer":"AlCo2.0CrFeMo0.5Ni was experimentally tested. The constituent phases of this alloy (Co-2.0) included BCC, FCC, and s phases. Its microstructure was a polygrain type without dendritic features, suggesting a narrow melting point range. Grain boundaries featured a thin layer of white s phase, and grain interiors contained white large stringers and a modulated structure primarily composed of FCC and BCC phases.","page_reference":"1, 11, 12, 16, 25, 26, 42","key_passage":"As cobalt content increases, the microstructure changes from dendrite to polygrain type and the constituent phases change from BCCþ s at x¼ 0.5 to BCCþ FCCþ s at x¼ 2.0 [1]. Table 1 shows the designated compositions of experimental AlCoxCrFeMo0.5Ni alloys (Co-x alloy hereafter represent the alloy with cobalt content x) [2]. Only three crystal structures: FCC (a¼ 3.60 Å), BCC (a¼ 2.87 Å) with a small ordered peak at around 318, and s phase (a¼ 8.94 Å and c¼ 4.65 Å) are identified [2]. This reveals the interesting phenomena that although AlCoxCrFeMo0.5Ni alloys have six principal elements, they exhibit a number of simple phases much less than seven phases allowed by Gibbs phase rule [23]. The Co-2.0 alloy further contains a FCC phase indicating that the element Co can suppress s phase and promote FCC phase [24]. Figures 2(d) and (e) show themicrostructure of Co-2.0 alloy with two magnifications. The alloy displays a polygrain structure without dendritic features [25]. Grain boundaries have thin layer of white s phase and grain interiors contain white large stringers around 50mm in length and a modulated structure between large stringers [25]. From XRD analysis, the modulated structure is composed of FCC and BCC since their XRD peak heights are similar [26]. With the increased content of Co, an FCC stabilizer, the crystal structure of AlCoxCrFeMo0.5Ni HEAs gradually changes from BCCþ s phase at x¼ 0.5 to BCCþ FCCþ s phase at x¼ 2.0 [7].","expected_retrieval":true} | |
| {"qid":"ed1a1ae7-c90c-4da9-8cfd-d770203dc27e","paper_id":"10.1002@adem.200900171.pdf","composition":"AlCo2.0CrFeMo0.5Ni","tag":"experimental details","question_type":"long_answer","question":"Based on literature, was AlCo2.0CrFeMo0.5Ni tested experimentally, and if so, what method was used to prepare the experimental AlCo2.0CrFeMo0.5Ni specimens?","ground_truth_answer":"AlCo2.0CrFeMo0.5Ni was tested experimentally. The specimens were prepared by arc-melting raw elemental materials (Al, Co, Cr, Fe, Ni with >99.5wt% purity) and a Fe-61.5wt% Mo master alloy in granular shape, under a protective argon atmosphere. Each sample was re-melted and re-solidified four times to ensure uniform composition. Specimens for hot hardness measurements were 1.5 mm thick and 10 mm in diameter, prepared through standard metallographic grinding and polishing, with a final polish using 1mm grade diamond paste.","page_reference":"7, 8, 10","key_passage":"Raw elemental material, Al, Co, Cr, Fe, and Ni with purity higher than 99.5wt% and master alloy, Fe-61.5wt% Mo, all in granular shape were melted to prepare the alloys by using arc-melting method under a protective atmosphere of argon [8]. Four times of re-melting and re-solidification were performed for each sample to assure the uniform composition [9]. The specimens for hot hardness measurements were 1.5 mm in thickness and 10 mm in diameter [10]. They were ground and polished by standard metallographic procedure. Final polish was done with diamond paste of 1mm grade [10].","expected_retrieval":true} | |
| {"qid":"16fa9f24-f2c5-44fd-b893-6b9df7c908b9","paper_id":"10.1002@adem.200900171.pdf","composition":"AlCo2.0CrFeMo0.5Ni","tag":"experimental results","question_type":"long_answer","question":"Has AlCo2.0CrFeMo0.5Ni been experimentally tested, and what notable results were obtained from testing the AlCo2.0CrFeMo0.5Ni alloy?","ground_truth_answer":"AlCo2.0CrFeMo0.5Ni was experimentally tested. It exhibited a room temperature Vickers hardness of Hv 596, representing a significant decrease from Co-1.5, primarily due to the inclusion of a soft FCC phase. Although it possessed the most negative softening coefficient among the compared alloys, indicating weaker resistance against softening, its hardness level remained higher than In 718 and In 718 H across all tested temperatures. It also outperformed T-800 at temperatures above 1000K, and had a transition temperature of 1050K.","page_reference":"1, 28, 35, 37, 43","key_passage":"The alloy hardness varies fromHv 788 at x¼ 0.5 to Hv 596 at x¼ 2.0 [1]. A great hardness decrease occurs from Hv 711 at x¼ 1.5 to Hv 596 at x¼ 2.0 [14]. As Co content increases, the alloy hardness decreases due to the decreased amount of s phase [11]. The values of transition temperature (TT), intrinsic hardness (A), and softening coefficient (B) calculated according to Westbrook are summarized in Table 3 [17]. Although Co-2.0 alloy possesses the most negative value of softening coefficient (BII) among all alloys compared, indicating that Co-2.0 alloy has the weakest resistance against softening, it still has a higher hardness level than In 718, In 718 H over all temperature range and than that of T-800 at temperatures above 1000K [18].","expected_retrieval":true} | |
| {"qid":"78b36a18-d5b1-48b0-a174-d39f4104cccd","paper_id":"10.1002@adem.200900171.pdf","composition":"AlCo0.5CrFeMo0.5Ni","tag":"material phases","question_type":"long_answer","question":"Was AlCo0.5CrFeMo0.5Ni tested experimentally, and if so, which material phases were observed during experiments for AlCo0.5CrFeMo0.5Ni?","ground_truth_answer":"AlCo0.5CrFeMo0.5Ni (Co-0.5) was experimentally tested. The material phases identified in the as-cast state for this alloy were BCC and s phases. Its microstructure showed dendrite, interdendrite, and eutectic structure. The Al-rich dendrite was initially a BCC phase that transformed into Cr- and Mo-rich white s phase after precipitating fine gray Al- and Ni-rich BCC phases during cooling. The gray interdendrite was an ordered BCC phase, and the eutectic structure consisted of a disordered gray BCC phase and s phase.","page_reference":"1, 11, 15, 17, 19, 20, 42","key_passage":"As cobalt content increases, the microstructure changes from dendrite to polygrain type and the constituent phases change from BCCþ s at x¼ 0.5 to BCCþ FCCþ s at x¼ 2.0 [1]. Table 1 shows the designated compositions of experimental AlCoxCrFeMo0.5Ni alloys (Co-x alloy hereafter represent the alloy with cobalt content x) [2]. Only three crystal structures: FCC (a¼ 3.60 Å), BCC (a¼ 2.87 Å) with a small ordered peak at around 318, and s phase (a¼ 8.94 Å and c¼ 4.65 Å) are identified [2]. The Co-0.5, Co-1.0, and Co-1.5 alloys are characterized as having BCC and s phases [3]. Figure 2(a) shows the microstructure of the Co-0.5 alloy, which has dendrite (labeled as A), interdendrite (labeled as B), and eutectic structure (labeled as C) [4]. The white phases in the dendrite and eutectic structure are similar in composition which shows Cr and Mo contents higher than those in the overall composition [5]. On the other hand, the fine gray phase inside the dendrite, the coarse gray interdendrite phase, and the gray one in the eutectic structure are all rich in Al and Ni, among which the gray interdendrite phase is even richer in Al and Ni than other gray phase [5]. From the XRD and composition analysis of constituent phases above, it leads to that the Al-rich dendrite of Co-0.5 alloy is a BCC phase in the beginning and then transformed into Cr- andMo-rich white s phase after precipitating out fine gray Al- and Ni-rich BCC phases (0.5 to 0.7mm in size) during the cooling stage [6]. The gray interdendrite with even higher Al content is the ordered BCC phase having small XRD ordered peak at around 318 [6]. The eutectic structure is composed of gray BCC phase and s phase in which gray BCC phase is a disordered one because it contains lower Al content [6]. With the increased content of Co, an FCC stabilizer, the crystal structure of AlCoxCrFeMo0.5Ni HEAs gradually changes from BCCþ s phase at x¼ 0.5 to BCCþ FCCþ s phase at x¼ 2.0 [7].","citation":"Hsu et al. 2009","expected_retrieval":true} | |
| {"qid":"9ce75d18-bbac-4903-9e48-b2569520c8c2","paper_id":"10.1002@adem.200900171.pdf","composition":"AlCo0.5CrFeMo0.5Ni","tag":"experimental details","question_type":"long_answer","question":"Based on literature, was AlCo0.5CrFeMo0.5Ni tested experimentally, and if so, what method was used to prepare the experimental AlCo0.5CrFeMo0.5Ni specimens?","ground_truth_answer":"AlCo0.5CrFeMo0.5Ni was tested experimentally. Raw elemental materials (Al, Co, Cr, Fe, and Ni with purity higher than 99.5wt%) and master alloy (Fe-61.5wt% Mo) were melted to prepare the alloys using an arc-melting method under a protective atmosphere of argon. Four times of re-melting and re-solidification were performed for each sample to assure uniform composition. Specimens for hot hardness measurements were 1.5 mm in thickness and 10 mm in diameter, which were ground and polished by standard metallographic procedure, with final polish done with diamond paste of 1mm grade.","page_reference":"7, 8, 10","key_passage":"Raw elemental material, Al, Co, Cr, Fe, and Ni with purity higher than 99.5wt% and master alloy, Fe-61.5wt% Mo, all in granular shape were melted to prepare the alloys by using arc-melting method under a protective atmosphere of argon [8]. Four times of re-melting and re-solidification were performed for each sample to assure the uniform composition [9]. The specimens for hot hardness measurements were 1.5 mm in thickness and 10 mm in diameter [10]. They were ground and polished by standard metallographic procedure. Final polish was done with diamond paste of 1mm grade [10].","expected_retrieval":true} | |
| {"qid":"e8128d90-e3f2-451b-b0ce-fadb7afc582b","paper_id":"10.1002@adem.200900171.pdf","composition":"AlCo0.5CrFeMo0.5Ni","tag":"experimental results","question_type":"long_answer","question":"Has AlCo0.5CrFeMo0.5Ni been experimentally tested, and what notable results were obtained from testing the AlCo0.5CrFeMo0.5Ni alloy?","ground_truth_answer":"AlCo0.5CrFeMo0.5Ni was experimentally tested. It exhibited the highest room temperature hardness of Hv 788 among the AlCoxCrFeMo0.5Ni alloys, attributed to its highest volume fraction of hard s phase. Despite similar hardness to Co-1.0, its crack length was much longer, indicating lower toughness due to its continuous hard s phase matrix. This alloy also demonstrated a high hot hardness of Hv 347 at 1273K, significantly higher than Ni-based superalloys In 718 and In 718 H by Hv 220. It showed a transition temperature of 1003K, higher than T-800 by about 200K, and the lowest softening coefficient, only half that of In 718, indicating excellent strength retention at high temperatures.","page_reference":"1, 27, 28, 30, 33, 35, 36, 43, 44","key_passage":"All the AlCoxCrFeMo0.5Ni alloys possess higher hardness level than that of Ni-based super-alloys In 718/In 718H from room temperature to 1273K [1]. Both alloys of x¼ 0.5 and 1.0 exhibit a transition temperature higher than that of Co-based alloy T-800 by about 200K [1]. They also have a high hot hardness of Hv 347 at 1273K, which is higher than those of In 718 and In718 H by Hv 220 [1]. The alloy hardness varies fromHv 788 at x¼ 0.5 to Hv 596 at x¼ 2.0 [1]. Alloy of x¼ 0.5 is the hardest one due to its highest volume fraction of hard s phase [11]. As Co content increases, the alloy hardness decreases due to the decreased amount of s phase [11]. AlCoxCrFeMo0.5Ni (x¼ 0.5 to 2.0) alloys exhibit a superior combination of hardness and toughness over the base alloys they derived from, AlxCoCrCuFeNi [12]. The hardest Co-0.5 alloy has a crack length 91mm similar to that of Al1.0CoCrCuFeNi and Al2.3CoCrCuFeNi alloys, but Co-0.5 alloy has a hardness of Hv 788much higher than the latter two having Hv 406 and Hv 603, respectively [13]. Co-0.5 and Co-1.0 alloy possess similar hardness but the crack length of Co-0.5 alloy is much longer than that of Co-1.0 [14]. This is attributable to their microstructure difference since Co-1.0 alloy has fine modulated microstructure in the dendrite and interdendrite which could substantially retard the crack propagation whereas Co-0.5 alloy has a continuous hard but brittle white s phase as its matrix among which coarse BCC gray phase disperses [15]. In addition, Co-0.5 and Co-1.0 alloys exhibit the highest hot hardness of about Hv 340 at 1273K, which is much higher than that, around Hv 127, of In 718 and In 718 H [16]. The values of transition temperature (TT), intrinsic hardness (A), and softening coefficient (B) calculated according to Westbrook are summarized in Table 3 [17]. Co-0.5 and Co-1.0 alloys have the least negative value of softening coefficient (BII), and its value is about half that of In 718, suggesting that Co-0.5 and Co-1.0 alloys could sustain its strength up to 1273K very effectively [18]. Co-0.5 and Co-1.0 alloys have a transition temperature higher than that of T-800 by around 200K [12]. They also exhibit a hot hardness of around Hv 343 at 1273K, which is much higher than Hv 127 of In 718 [12].","expected_retrieval":true} | |
| {"qid":"a7c849d2-6da2-4a72-80ac-a774ad12ed23","paper_id":"10.1002@adem.200900171.pdf","composition":"AlCo1.0CrFeMo0.5Ni","tag":"material phases","question_type":"long_answer","question":"If AlCo1.0CrFeMo0.5Ni was tested experimentally, which material phases were found during experiments?","ground_truth_answer":"AlCo1.0CrFeMo0.5Ni was tested experimentally. This alloy (Co-1.0) was characterized by having BCC and s phases in its as-cast state. It exhibited a simple dendritic structure, consisting of dendrite and interdendrite, both displaying a modulated structure. The dendrite was rich in Al and Ni with BCC structure, and the interdendrite was rich in Cr and Mo, also with BCC structure, precipitating s phase during cooling.","page_reference":"1, 11, 15, 21, 24, 42","key_passage":"As cobalt content increases, the microstructure changes from dendrite to polygrain type and the constituent phases change from BCCþ s at x¼ 0.5 to BCCþ FCCþ s at x¼ 2.0 [1]. Table 1 shows the designated compositions of experimental AlCoxCrFeMo0.5Ni alloys (Co-x alloy hereafter represent the alloy with cobalt content x) [2]. Only three crystal structures: FCC (a¼ 3.60 Å), BCC (a¼ 2.87 Å) with a small ordered peak at around 318, and s phase (a¼ 8.94 Å and c¼ 4.65 Å) are identified [2]. The Co-0.5, Co-1.0, and Co-1.5 alloys are characterized as having BCC and s phases [3]. The Co-1.0 andCo-1.5 alloys contain no eutectic regions but exhibit a simple dendritic structure composing of dendrite (labeled as A) and interdendrite (labeled as B) [19]. It can be seen that both dendrite and interdendrite display modulated structure like the spinodal decomposition structure [19]. The precipitation results in modulated structures (white phase is s and gray phase is BCC) both in dendrite and interdendrite [20]. With the increased content of Co, an FCC stabilizer, the crystal structure of AlCoxCrFeMo0.5Ni HEAs gradually changes from BCCþ s phase at x¼ 0.5 to BCCþ FCCþ s phase at x¼ 2.0 [7].","expected_retrieval":true} | |
| {"qid":"60d6feb2-51c5-42ca-bdd9-138dc2abbe29","paper_id":"10.1002@adem.200900171.pdf","composition":"AlCo1.0CrFeMo0.5Ni","tag":"experimental details","question_type":"long_answer","question":"Was AlCo1.0CrFeMo0.5Ni tested, and if so, how were the experimental AlCo1.0CrFeMo0.5Ni specimens prepared?","ground_truth_answer":"AlCo1.0CrFeMo0.5Ni was tested experimentally. Specimens were prepared by melting raw elemental materials (Al, Co, Cr, Fe, Ni with >99.5wt% purity) and master alloy (Fe-61.5wt% Mo) using an arc-melting method under a protective argon atmosphere. To ensure uniform composition, each sample underwent four re-melting and re-solidification cycles. For hot hardness measurements, specimens were 1.5 mm thick and 10 mm in diameter, ground and polished according to standard metallographic procedures, with final polishing done using 1mm grade diamond paste.","page_reference":"7, 8, 10","key_passage":"Raw elemental material, Al, Co, Cr, Fe, and Ni with purity higher than 99.5wt% and master alloy, Fe-61.5wt% Mo, all in granular shape were melted to prepare the alloys by using arc-melting method under a protective atmosphere of argon [8]. Four times of re-melting and re-solidification were performed for each sample to assure the uniform composition [9]. The specimens for hot hardness measurements were 1.5 mm in thickness and 10 mm in diameter [10]. They were ground and polished by standard metallographic procedure. Final polish was done with diamond paste of 1mm grade [10].","expected_retrieval":true} | |
| {"qid":"3fba63d3-24a0-45c3-a80d-def9614afe40","paper_id":"10.1002@adem.200900171.pdf","composition":"AlCo1.0CrFeMo0.5Ni","tag":"experimental results","question_type":"long_answer","question":"For AlCo1.0CrFeMo0.5Ni, was it tested experimentally, and what were the main findings obtained from testing this alloy?","ground_truth_answer":"AlCo1.0CrFeMo0.5Ni was tested experimentally. It exhibited a room temperature Vickers hardness of Hv 770. While it had similar hardness to Co-0.5, its crack length was significantly shorter (about 13mm vs. 91mm for Co-0.5), indicating superior fracture toughness, which is attributed to its fine modulated microstructure that retards crack propagation. This alloy also showed a high hot hardness of approximately Hv 340 at 1273K, much higher than In 718, and a transition temperature of 995K, demonstrating excellent resistance to softening up to high temperatures.","page_reference":"1, 27, 28, 30, 33, 35, 36, 37, 44","key_passage":"All the AlCoxCrFeMo0.5Ni alloys possess higher hardness level than that of Ni-based super-alloys In 718/In 718H from room temperature to 1273K [1]. Both alloys of x¼ 0.5 and 1.0 exhibit a transition temperature higher than that of Co-based alloy T-800 by about 200K [1]. They also have a high hot hardness of Hv 347 at 1273K, which is higher than those of In 718 and In718 H by Hv 220 [1]. Furthermore, even the best alloy Al2.0CoCrCuFeNi having a crack length about 20mmand a hardness of Hv 566 due to its modulated spinodal structure of B2 ordered BCC and BCC phases is still inferior to Co-1.0 alloy having a crack length about 13mmand a hardness of Hv 770 [13]. Co-0.5 and Co-1.0 alloy possess similar hardness but the crack length of Co-0.5 alloy is much longer than that of Co-1.0 [14]. This is attributable to their microstructure difference since Co-1.0 alloy has fine modulated microstructure in the dendrite and interdendrite which could substantially retard the crack propagation [15]. Evidences have shown that s phase is the hardest phase sincemicrohardnessmeasurements on the dendrite (with less s phase) and the interdendrite (with more s phase) in the Co-1.0 alloy give Hv 634 and Hv 824, respectively [21]. In addition, Co-0.5 and Co-1.0 alloys exhibit the highest hot hardness of about Hv 340 at 1273K, which is much higher than that, around Hv 127, of In 718 and In 718 H [16]. The values of transition temperature (TT), intrinsic hardness (A), and softening coefficient (B) calculated according to Westbrook are summarized in Table 3 [17]. Co-0.5 and Co-1.0 alloys have the least negative value of softening coefficient (BII), and its value is about half that of In 718, suggesting that Co-0.5 and Co-1.0 alloys could sustain its strength up to 1273K very effectively [18]. Co-0.5 and Co-1.0 alloys have a transition temperature higher than that of T-800 by around 200K [12]. They also exhibit a hot hardness of around Hv 343 at 1273K, which is much higher than Hv 127 of In 718 [12].","expected_retrieval":true} | |