# Al–Mo–Ti system > Al–Mo–Ti system: 29 accepted literature values (invariant reaction 16, phase equilibrium 13) and 0 calculated phase diagram(s) from ORCHID, each value with evidence class, source, page and quote. HTML: https://data.orchid-project.org/systems/AL-MO-TI.html · Markdown: https://data.orchid-project.org/systems/AL-MO-TI.md 29 accepted literature values from 1 paper(s) (experimental 11, model 18); 0 calculated phase diagram(s). Data: [JSON](https://data.orchid-project.org/literature/systems/AL-MO-TI.json) · [CSV](https://data.orchid-project.org/systems/AL-MO-TI.csv) · [interactive explorer](https://orchid-project.org/data-explorer/#AL-MO-TI) · [papers (bibliography)](https://data.orchid-project.org/bibliography/pages/systems/AL-MO-TI.html) · [Markdown](https://data.orchid-project.org/systems/AL-MO-TI.md) Table: Accepted values by evidence class | Evidence class | Values | |---|---:| | experimental | 11 | | model | 18 | Table: Accepted values by property group | Property group | Values | |---|---:| | invariant reaction | 16 | | phase equilibrium | 13 | ## Invariant reactions (literature) Table: Invariant reactions reported in the literature for the Al–Mo–Ti system (16) | T (K) | Reaction / phases | Compositions (mole fraction) | Class | Source | Location | Quote | |---:|---|---|---|---|---|---| | 1800 | Liquid + Al63Mo37 -> β + Al8Mo3 | Liquid: Al 0.649, Mo 0.337, Ti 0.014; Al63Mo37: Al 0.63, Mo 0.37, Ti 0; Al8Mo3: Al 0.727273, Mo 0.272727, Ti 0 | model | [1] Cupid 2010 | Table 3, p. 9, row 1; `ORC-6LRZJ4MLZY` | | | 1773 | Liquid + Al63Mo37 -> β + Al8Mo3 | Al63Mo37: Al 0.63, Mo 0.37, Ti 0; Al8Mo3: Al 0.727273, Mo 0.272727, Ti 0 | experimental | [1] Cupid 2010; _cites Tretyachenko 2005_ | Table 3, p. 9, row 2; `ORC-MUB2LDD5HX` | | | 1743 | Liquid + Al8Mo3 -> β + η | Al8Mo3: Al 0.727273, Mo 0.272727, Ti 0 | experimental | [1] Cupid 2010; _cites Tretyachenko 2005_ | Table 3, p. 9, row 6; `ORC-LPKMRGXRLF` | | | 1713 | Liquid + α -> β + γ | | experimental | [1] Cupid 2010; _cites Tretyachenko 2005_ | Table 3, p. 9, row 4; `ORC-NDK33CPHYW` | | | 1701 | Liquid + α -> β + γ | Liquid: Al 0.551, Mo 0.015, Ti 0.435 | model | [1] Cupid 2010 | Table 3, p. 9, row 3; `ORC-ICGJZ5LNXT` | | | 1676 | Liquid + Al8Mo3 -> β + η | Liquid: Al 0.634, Mo 0.251, Ti 0.115; Al8Mo3: Al 0.727273, Mo 0.272727, Ti 0 | model | [1] Cupid 2010 | Table 3, p. 9, row 5; `ORC-7MTRUHLIWK` | | | 1673 | Liquid + ζ -> η + γ | | experimental | [1] Cupid 2010; _cites Tretyachenko 2005_ | Table 3, p. 9, row 8; `ORC-BZD4DIODBL` | | | 1643 | Liquid -> γ + η + β | | experimental | [1] Cupid 2010; _cites Tretyachenko 2005_ | Table 3, p. 9, row 10; `ORC-BVA2AL6Y5Q` | | | 1627 | Liquid + ζ -> η + γ | Liquid: Al 0.674, Mo 0.024, Ti 0.302 | model | [1] Cupid 2010 | Table 3, p. 9, row 7; `ORC-PYPC5VEGAZ` | | | 1569 | Liquid -> γ + η + β | Liquid: Al 0.554, Mo 0.082, Ti 0.334 | model | [1] Cupid 2010 | Table 3, p. 9, row 9; `ORC-EUQZZOXYLC` | | | 1494 | Liquid + Al8Mo3 -> η + Al3Mo | Liquid: Al 0.952, Mo 0.047, Ti 0.001; Al8Mo3: Al 0.727273, Mo 0.272727, Ti 0 | model | [1] Cupid 2010 | Table 3, p. 9, row 11; `ORC-RRY6AKUDXM` | | | 1425 | Liquid + Al3Mo -> η + Al4Mo | Liquid: Al 0.967, Mo 0.033, Ti 0; Al4Mo: Al 0.8, Mo 0.2, Ti 0 | model | [1] Cupid 2010 | Table 3, p. 9, row 12; `ORC-KH2EMHKO7A` | | | 1270 | Liquid + Al4Mo -> η + Al17Mo4 | Liquid: Al 0.994, Mo 0.006, Ti 0; Al4Mo: Al 0.8, Mo 0.2, Ti 0 | model | [1] Cupid 2010 | Table 3, p. 9, row 13; `ORC-4ZZB2H3P4Y` | | | 1213 | Liquid + Al17Mo4 -> η + Al22Mo5 | Liquid: Al 0.998, Mo 0.002, Ti 0 | model | [1] Cupid 2010 | Table 3, p. 9, row 14; `ORC-JLMPDSXUSQ` | | | 1119 | Liquid + Al22Mo5 -> η + Al5Mo | Liquid: Al 0.998, Mo 0.002, Ti 0; Al5Mo: Al 0.833333, Mo 0.166667, Ti 0 | model | [1] Cupid 2010 | Table 3, p. 9, row 15; `ORC-65MZEHPRB5` | | | 985 | Liquid + η + Al5Mo -> Al12Mo | Liquid: Al 0.9997, Mo 3.000e-4, Ti 0; Al5Mo: Al 0.833333, Mo 0.166667, Ti 0; Al12Mo: Al 0.923077, Mo 0.076923, Ti 0 | model | [1] Cupid 2010 | Table 3, p. 9, row 16; `ORC-KYUHMTZ3FS` | | ## Other properties ### Phase equilibrium (13) Table: Phase equilibrium, Al–Mo–Ti system | Property | Value | T (K) | Phases / composition | Class | Source | Location | Quote | |---|---:|---:|---|---|---|---|---| | Phase assemblage | | 1073 | a; _alloy: Al 0.025, Mo 0.025, Ti 0.95_ | experimental | [1] Cupid 2010; _cites Eremenko 1990_ | p. 3; `ORC-Y7OPQQIKTO` | “The Ti-rich a single phase was also observed in an alloy 95 at.%Tie2.5 at. %Ale2.5 at.%Mo which was heat treated at 1073 K for 222 h and quenched \[53\].” | | Phase assemblage | | 1198 | d-AlMo3; _alloy: Al 0.24, Mo 0.58, Ti 0.18_ | model | [1] Cupid 2010; _cites Hansen 1970_ | p. 3; `ORC-QOXZKAPNIY` | “Additionally, an alloy of composition 18 at.%Tie24 at.%Ale58 at.% Mo, which was heat treated at 1198 K and quenched, contained only the d-AlMo3 phase \[48\], which indicates that the d-AlMo3 phase extends to at least 18 at.%Ti at 1198 K in the TieAleMo system.” | | Phase assemblage | | 1198 | h-(Ti,Mo)Al3; _alloy: Al 0.75, Mo 0.125, Ti 0.125_ | model | [1] Cupid 2010; _cites Hansen 1970_ | p. 3; `ORC-7R5IAGYHYB.27b9b7` | “Hansen and Raman \[48\] showed that alloys of composition 26 at.%Tie64 at.%Ale10 at.%Mo, 16 at.%Tie68 at.% Ale16 at.%Mo, and 12.5 at.%Tie75 at.%Ale12.5 at.%Mo were all single phase h-(Ti,Mo)Al3 at 1198 K, and the h-(Ti,Mo)Al3 phase was found to extend to Mo compositions as high as 20 at.%Mo and Al compositions as low as 62 at.%Al at 1198 K \[48\].” | | Phase assemblage | | 1198 | h-(Ti,Mo)Al3; _alloy: Al 0.68, Mo 0.16, Ti 0.16_ | model | [1] Cupid 2010; _cites Hansen 1970_ | p. 3; `ORC-7R5IAGYHYB.303370` | “Hansen and Raman \[48\] showed that alloys of composition 26 at.%Tie64 at.%Ale10 at.%Mo, 16 at.%Tie68 at.% Ale16 at.%Mo, and 12.5 at.%Tie75 at.%Ale12.5 at.%Mo were all single phase h-(Ti,Mo)Al3 at 1198 K, and the h-(Ti,Mo)Al3 phase was found to extend to Mo compositions as high as 20 at.%Mo and Al compositions as low as 62 at.%Al at 1198 K \[48\].” | | Phase assemblage | | 1198 | h-(Ti,Mo)Al3; _alloy: Al 0.64, Mo 0.1, Ti 0.26_ | model | [1] Cupid 2010; _cites Hansen 1970_ | p. 3; `ORC-7R5IAGYHYB.ad304e` | “Hansen and Raman \[48\] showed that alloys of composition 26 at.%Tie64 at.%Ale10 at.%Mo, 16 at.%Tie68 at.% Ale16 at.%Mo, and 12.5 at.%Tie75 at.%Ale12.5 at.%Mo were all single phase h-(Ti,Mo)Al3 at 1198 K, and the h-(Ti,Mo)Al3 phase was found to extend to Mo compositions as high as 20 at.%Mo and Al compositions as low as 62 at.%Al at 1198 K \[48\].” | | Phase assemblage | | 1198 | s; _alloy: Al 0.41, Mo 0.33, Ti 0.26_ | model | [1] Cupid 2010; _cites Hansen 1970_ | p. 4; `ORC-JSJZ54DYRF` | “Hansen and Raman \[48\] found the ternary s phase in the single phase alloy of composition 26 at.%Tie41 at.%Ale33 at.%Mo at 1198 K.” | | Phase assemblage | | 1273 | b0; _alloy: Al 0.25, Mo 0.25, Ti 0.5_ | experimental | [1] Cupid 2010; _cites Singh 2007_ [doi](https://doi.org/10.1080/14786430701654378) | p. 4; `ORC-HS7LQHYH5W` | “Singh et al. \[59\] performed Rietveld refinement of X-ray and neutron diffraction data from an alloy of composition 50 at.%Tie25 at.%Ale25 at.%Mo which was homogenized at 1273 K and furnace cooled. The alloy was found to contain the b0 phase, and Rietveld refinement of the data showed that Ti atoms occupy A sites and Al and Mo atoms occupy the B sites in the CsCl structure.” | | Phase assemblage | | 1673 | a; _alloy: Al 0.48, Mo 0.02, Ti 0.5_ | experimental | [1] Cupid 2010; _cites Singh 1997_ [doi](https://doi.org/10.1007/s11661-997-0106-6) | p. 3; `ORC-HVNTGGB7RH` | “Although the maximum solubility of Mo in the a phase has not been measured, Singh and Banerjee \[52\] showed that an alloy of composition 50 at.%Tie48 at.%Ale2 at.%Mo is in the single phase a field at 1673 K and suggested that the a phase field extends to an alloy of composition 44 at.%Tie50 at.%Ale6 at.%Mo at 1673 K.” | | Phase assemblage | | 1673 | b + Al8Mo3 + d-AlMo3; _alloy: Al 0.52, Mo 0.45, Ti 0.03_ | experimental | [1] Cupid 2010; _cites Nino 2003_ [doi](https://doi.org/10.1016/s0966-9795%2803%2900049-9) | p. 3; `ORC-KBQTU5VSNY` | “For example, the equilibrium b þ Al8Mo3 þ d-AlMo3 tie-triangle data for an alloy of composition 3 at.%Tie52 at.%Ale45 at.%Mo, which was heat treated at 1673 K and quenched, showed that the Al8Mo3 phase dissolved 1 at.%Ti and that the d-AlMo3 phase dissolved 2.7 at.%Ti \[15\].” | | Phase assemblage | | 1773 | b; _alloy: Al 0.52, Mo 0.45, Ti 0.03_ | experimental | [1] Cupid 2010; _cites Nino 2003_ [doi](https://doi.org/10.1016/s0966-9795%2803%2900049-9) | p. 4; `ORC-5C4ROP6R3A.73b0d9` | “For example, although the alloy of composition 3 at.%Tie52 at.% Ale45 at.%Mo should be single phase b at 1773 K \[15\], this alloy is calculated in the liquid þ b þ Al63Mo37 three phase field at the same temperature and is located in the primary crystallization field of the d phase on the calculated liquidus surface \[16\].” | | Phase assemblage | | 1773 | b; _alloy: Al 0.52, Mo 0.45, Ti 0.03_ | experimental | [1] Cupid 2010; _cites Nino 2003_ [doi](https://doi.org/10.1016/s0966-9795%2803%2900049-9) | p. 4; `ORC-L4ZOMWE37P` | “The results of Nino et al. \[15\] also confirmed that the b phase is continuous in the solid state solution from the TieMo binary to the AleMo binary since an alloy of composition 3 at.%Tie52 at.%Ale45 at.%Mo, with only 3 at.%Ti, showed a single phase b microstructure following heat treatment at 1773 K and quenching \[15\].” | | Phase assemblage | | 1773 | b; _alloy: Al 0.52, Mo 0.45, Ti 0.03_ | model | [1] Cupid 2010 | p. 8; `ORC-XB3IFVR4JN` | “Fig. 4 shows the calculated isothermal section at 1773 K. The alloy of composition 3 at.%Tie52 at.%Ale45 at.%Mo is calculated in the single phase b field, which is in very good agreement with the experimental work of Nino et al. \[15\].” | | Phase assemblage | | 1773 | liquid + b + Al63Mo37; _alloy: Al 0.52, Mo 0.45, Ti 0.03_ | model | [1] Cupid 2010; _cites Cupid 2009_ [doi](https://doi.org/10.3139/146.110015) | p. 4; `ORC-5C4ROP6R3A.1abf70` | “For example, although the alloy of composition 3 at.%Tie52 at.% Ale45 at.%Mo should be single phase b at 1773 K \[15\], this alloy is calculated in the liquid þ b þ Al63Mo37 three phase field at the same temperature and is located in the primary crystallization field of the d phase on the calculated liquidus surface \[16\].” | ## Sources Reporting papers the values were read from (a value cited from another work names that work in its row). 1. Damian M. Cupid, Olga Fabrichnaya, Fereshteh Ebrahimi, Hans J. Seifert, Thermodynamic assessment of the Al–Mo system and of the Ti–Al–Mo System from 0 to 20at.% Ti, Intermetallics 18, 1185-1196 (2010). [doi:10.1016/j.intermet.2010.03.010](https://doi.org/10.1016/j.intermet.2010.03.010) ## Please cite - R. Arróyave, J. Saal, D. Shin, ORCHID-Values: thermodynamic and phase-equilibrium values read from the literature (version 2026.10; Version 1, machine-extracted), Zenodo (2026). https://doi.org/10.5281/zenodo.23735569 - R. Arróyave, J. Saal, D. Shin, ORCHID data: umbrella record of the ORCHID datasets (version 2026.10; Version 1, machine-extracted), Zenodo (2026). https://doi.org/10.5281/zenodo.23736065 Also cite the original source of every value you use (paper_citation / paper_doi, and cited_dois for values the paper cites from earlier work); B. Hallstedt, The SGTE collection of binary datasets, Calphad 89 (2025) 102833, https://doi.org/10.1016/j.calphad.2025.102833 (CC BY 4.0), and the original assessment named in each file; A. Jain et al., The Materials Project: A materials genome approach to accelerating materials innovation, APL Materials 1 (2013) 011002, https://doi.org/10.1063/1.4812323 (CC BY 4.0); J. E. Saal et al., JOM 65 (2013) 1501, https://doi.org/10.1007/s11837-013-0755-4 and S. Kirklin et al., npj Comput. Mater. 1 (2015) 15010, https://doi.org/10.1038/npjcompumats.2015.10 (CC BY 4.0). Version 1, machine-extracted: values were read by language-model readers constrained to quote their source and checked automatically, and the release was then audited on the printed pages by adversarial audits, an independent second review of fit-facing records and a preliminary human review of a frozen sample. Flags such as accepted and ESPEI-ready record screening results, not certification; known issues are listed in the release notes. ```bibtex @misc{orchid_literature_2026, author = {Arr{\'o}yave, Raymundo and Saal, James and Shin, Dongwon}, title = {{ORCHID-Values: thermodynamic and phase-equilibrium values read from the literature}}, version = {2026.10}, publisher = {Zenodo}, year = {2026}, doi = {10.5281/zenodo.23735569}, url = {https://doi.org/10.5281/zenodo.23735569}, note = {Version 1, machine-extracted} } @misc{orchid_data_2026, author = {Arr{\'o}yave, Raymundo and Saal, James and Shin, Dongwon}, title = {{ORCHID data: umbrella record of the ORCHID datasets}}, version = {2026.10}, publisher = {Zenodo}, year = {2026}, doi = {10.5281/zenodo.23736065}, url = {https://doi.org/10.5281/zenodo.23736065}, note = {Version 1, machine-extracted} } ``` --- Derived data CC BY 4.0 ([licence](https://creativecommons.org/licenses/by/4.0/)): cite ORCHID ([CITATION.cff](https://data.orchid-project.org/CITATION.cff)) and the original sources. Quotes are short excerpts kept so that each value can be checked; they remain under the publishers' copyright and are not relicensed. Source papers, page images and full text are not redistributed. Field reference: [SCHEMA.md](https://data.orchid-project.org/literature/SCHEMA.md). Machine-readable guide: [llms.txt](https://data.orchid-project.org/llms.txt). Found an error? The report link of a value (Markdown: its id, ORC-..., in the Location column) opens a pre-filled GitHub issue, https://github.com/orchid-calphad/orchid-data/issues/new?template=report-value-error.yml&record_id=\, carrying only the record id, source and value; [how to contribute](https://orchid-project.org/contribute/).