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REVIEW 3 major objections 5 minor 60 references

Splat formation and microstructure of solution precursor thermal sprayed Nb-doped titanium oxide coatings

T0 review · 3 major / 5 minor · reviewed 2026-08-14 · deepseek-v4-flash

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Pith's one-line read Higher flame power raises the anatase phase content of solution-precursor sprayed Nb-doped titanium oxide coatings, contrary to the usual high-temperature expectation.

desk verdict A solid first demonstration of SP-HVOF Nb-doped TiO2 with a plausible but under-supported flame-power/anatase trend. read the letter →

arxiv 1908.04669 v1 pith:ALM56AAJ submitted 2019-08-13 physics.app-ph

Daniel Tejero-Martin , Zdenek Pala , Simon Rushworth , Tanvir Hussain This is my paper · ORCID
classification physics.app-ph
keywords solutionprecursorthermalsprayHVOFniobium-dopedtitaniumdioxideanataserutilesinglesplatphasecontentporosity
verification ladder T0 review T1 audit T2 compute T3 formal

The pith

A machine-rendered reading of the paper's core claim, the machinery that carries it, and where it could break.

The reading

This paper presents a counterintuitive result in solution precursor high-velocity oxy-fuel spraying: niobium-doped titanium dioxide coatings made with a hotter flame contain more of the anatase phase, normally the less stable form at high temperature, not more rutile. Three independent x-ray diffraction analyses put the anatase content at about 5% for a 25 kW flame and about 19% for a 75 kW flame, with porosity dropping at the higher power. The proposed cause is that the hotter flame fully melts the in-flight material, and its rapid cooling on impact favours anatase nucleation from the melt, while niobium doping additionally slows the usual anatase-to-rutile conversion. If this is right, flame power becomes a practical control dial for phase content and density in coatings deposited from solution precursors.

What carries the argument

The analysis hinges on three phase-quantification routes applied to the same x-ray diffraction data: Rietveld refinement, a whole-pattern fitting method; a peak-height formula based on the anatase (101) and rutile (110) reflections; and a peak-area formula for the same reflections. Together they establish the direction of the phase change rather than relying on one method. The physical explanation is carried by a proposed in-flight transformation model: primary and secondary droplet fragmentation, solvent evaporation, precipitation or shell formation, pyrolysis and sintering, melting, and splat impact. The model is anchored by swipe-test single splats collected at stand-off distances of 65, 85, and 105 mm, and by TGA-DSC measurements that identify the pyrolysis, crystallisation, and anatase-to-rutile transformation temperatures of the precursor.

What would settle it

Spray the same Nb-doped precursor at 25, 50, and 75 kW while holding the hydrogen-to-oxygen ratio fixed, and repeat each condition several times; if the anatase content does not rise monotonically with flame power, or if run-to-run scatter is as large as the 5.1% to 18.7% gap, the claimed causal role of flame power would be refuted.

Watch

Extended reading notes

Core claim

The discovery claimed is that flame power controls phase selection in solution precursor HVOF of Nb-doped TiO2: raising the flame power from 25 kW to 75 kW raises the anatase content from 5.1% to 18.7% as measured by Rietveld refinement, with peak-height and peak-area methods showing the same direction, while coating porosity falls sharply. The paper interprets this through the melting state of the material on impact. At 25 kW the simulated flame temperature, about 1880 °C, is barely above the melting point of TiO2, so solid, sintered particles arrive only partially molten and build a porous coating; at 75 kW, about 2480 °C, particles melt completely and the rapid cooling of splats on the substrate favours anatase nucleation directly from the melt. Niobium doping is treated as a contributing factor because it inhibits the anatase-to-rutile transformation, but not as the primary cause. Single-splat collections at three stand-off distances show the progression from droplets to precipitated, pyrolysed, sintered, and finally molten material, with niobium-rich outer layers on the splats.

Load-bearing premise

The central claim assumes that the two spray runs differed only in flame power, but the lower-power run used 78 l/min hydrogen with 182 l/min oxygen and the higher-power run used 229 l/min hydrogen with 533 l/min oxygen, so gas velocity, momentum, stoichiometry, and residence time also changed; if one of those co-varying factors drives the phase or porosity difference, the flame-power claim does not stand alone.

Editorial extensions

If this is right

  • Flame power can be used as a process parameter to tune coating density: low power yields porous, loosely bonded coatings, and high power yields dense coatings with fully molten splats.
  • Phase content in solution-precursor titania is not monotonic in the usual thermodynamic direction; hotter spraying can increase the fraction of anatase, so process design should not assume that high temperature means rutile.
  • The proposed in-flight transformation model gives a concrete route from a liquid precursor to a final coating, predicting that stand-off distance controls the balance between solid particulates and molten splats.
  • Quantifying titania phases by three independent XRD methods provides a template for checking phase claims in thermal spray coatings where peak broadening and small grain sizes complicate single-method results.

Reading between the lines

Editorial extensions of the paper, not claims the author makes directly.

  • If the melt-nucleation interpretation is right, the same higher-power/higher-anatase trend should appear in other dopant-titania combinations sprayed from solution precursors, provided the dopant does not suppress anatase nucleation; that is a testable prediction the paper does not make.
  • Because the 25 kW and 75 kW runs co-varied fuel and oxygen flows, a cleaner version of this study would separate flame enthalpy from gas velocity and residence time, for example by varying total gas flow at fixed hydrogen-to-oxygen ratio while tracking droplet momentum.
  • The paper's constant niobium signal across flame powers suggests that doping level and phase content can be set somewhat independently, which points toward tuning conductivity and photocatalysis separately in Nb-doped titania coatings; the paper does not pursue those functional consequences.
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Editorial analysis

A structured set of objections, weighed in public.

Desk editor's note, referee report, and a circularity audit.

Referee Report

3 major / 5 minor

Summary. The paper reports the first deposition of niobium-doped TiO2 coatings by solution precursor high-velocity oxy-fuel (SP-HVOF) spraying at two nominal flame powers, 25 kW and 75 kW. The coatings were characterized by SEM/EDS and XRD, with anatase content quantified by Rietveld refinement, peak-height, and peak-area methods. Single-splat swipe tests at stand-off distances of 65, 85, and 105 mm, together with TGA/DSC of the precursor and dried powder, are used to propose a qualitative model of precursor breakup, solvent evaporation, precipitation, pyrolysis, sintering, melting, and splat formation. The central claim is that increasing flame power increases anatase content from 5.1% to 18.7% (Rietveld) and reduces coating porosity, and that this trend is confirmed by all three XRD quantification methods.

Significance. If the central claim holds, the paper would establish flame power as a practical control handle for phase content in SP-HVOF of Nb-doped TiO2, which matters for photocatalytic, sensing, and transparent-conductive applications. The work is also useful as a first demonstration of SP-HVOF for this material system, and the swipe-test series at three stand-off distances is a well-designed qualitative probe of in-flight particle evolution. Credit is due for explicitly acknowledging several limitations of the XRD quantification, such as the use of undoped ICSD structures and the presence of unquantified amorphous content. However, the causal attribution to flame power rests on a single pair of spray runs that differ in multiple gas-flow parameters, and the three 'independent' quantification methods share the same reflections and calibration assumptions, so the headline claim is not yet established at the level of confidence implied by the conclusions.

major comments (3)
  1. [Section 2.1 and Section 3.1] The causal attribution of the observed phase and porosity differences to flame power is not supported by the experimental design. The 25 kW run used 78 l/min H2 and 182 l/min O2, while the 75 kW run used 229 l/min H2 and 533 l/min O2, so the total gas flow increases by roughly a factor of three. Nozzle exit velocity, gas momentum, droplet Weber and Reynolds numbers, secondary fragmentation, in-flight residence time, and convective heat transfer all co-vary with the combustion enthalpy. With one spray per condition and no replicate runs or error bars, the statement in the conclusions that 'an increase in flame power equated to an increase in the anatase phase content' overstates a two-point correlation. The authors should either add a single-variable or factorial spray matrix, or clearly reframe the claim as a correlation between the full 25 kW/75 kW parameter sets rather than a causal effect of flame power alone.
  2. [Section 3.1.1, Equations (1) and (2), Figure 4] The claim that 'three calculation methods confirmed' the anatase increase is not fully justified because the three methods are not independent. The peak-height method (Eq. 1) and the peak-area method (Eq. 2) are both applied to the same anatase (101) and rutile (110) reflections, and both use calibration constants determined for undoped titania in other spray processes. The Rietveld refinement also used undoped ICSD structures and did not quantify the amorphous content that the text itself mentions as a possible cause of peak broadening. The agreement among the three methods therefore reflects shared systematic biases as well as any real phase-content difference. The authors should report the refined lattice parameters and goodness-of-fit values, quantify or bound the amorphous content, and provide uncertainties on the reported 5.1% and 18.7% values.
  3. [Section 3.1 and Figure 1] The porosity reduction at higher flame power is presented as a central microstructural result, but it is supported only by qualitative inspection of BSE-SEM cross-sections in Figure 1. No image-analysis-based porosity measurements, standard deviations, or replicate cross-sections are provided. A quantitative porosity estimate would strengthen the manuscript and is needed to support the statement that flame power is an effective way to modify coating microstructure.
minor comments (5)
  1. [Section 3 title] The heading 'Results and Conclusions' is unusual; if the conclusions are collected in Section 4, the third section should be titled 'Results and Discussion'.
  2. [Figure 8 caption] The caption states 'All images were taken at 20 kW'; this should read '20 kV' to refer to the SEM accelerating voltage.
  3. [Section 2.1] The sentence 'In both cases the stand-off distance was 85 mm' should clarify that this applies to the coating deposition runs, since the swipe tests in the same section use stand-off distances of 65, 85, and 105 mm.
  4. [Section 3.2.1] The statement that solid features are absent at larger stand-off distances is too strong, since the 85 mm swipe sample clearly contains solid particulates mixed with molten splats in Figure 8; the text should distinguish between craters from solid-particle impacts and the presence of solid particles generally.
  5. [Equations (1) and (2)] The numerical constants in Equations (1) and (2) are cited to prior literature, but the manuscript should state explicitly that these constants were derived for undoped titania and may not transfer directly to Nb-doped SP-HVOF coatings with different crystallite sizes.

Circularity Check

0 steps flagged · score 0.0 of 10

No circular derivation: phase quantification is externally calibrated and the proposed mechanism is a post hoc interpretation, not an input to the measurements.

full rationale

The paper's central quantitative results are the anatase contents (5.1% vs 18.7% by Rietveld, with the same direction by peak-height and peak-area methods) for two coatings sprayed at 25 kW and 75 kW. These values are obtained from XRD patterns using Rietveld refinement with ICSD structural models and from published calibration formulas (Berger-Keller et al.; Yang et al.), i.e., externally fixed constants not fitted to this dataset, so the phase fractions are not self-defined outputs. The proposed explanation (higher flame temperature melts in-flight solids; rapid cooling nucleates anatase, citing Li and Ishigaki) is a plausible post hoc mechanism and does not enter the XRD quantification. The process model in Section 3.2 is descriptive and derived from TGA/DSC and swipe-test images, not from the phase percentages. Self-citations (Refs 38, 39, 43) are used for experimental setup details and simulated flame temperatures; they are not invoked as a uniqueness theorem or as the source of the phase-counting equations. The principal weakness is experimental rather than circular: the two runs differ in total gas flow as well as flame power, with one run per condition, so the causal attribution to flame power is not fully controlled; this is a validity/correctness concern, not a reduction of the derivation to its inputs. No circular step can be quoted in the paper.

Assumptions & free parameters 3 free parameters · 4 assumptions · 0 invented entities

The central claim rests on external calibration constants, undoped crystal structure models in Rietveld refinement, simulated flame temperatures from an in-house numerical study, and an unverified controlled-variable assumption for the two flame conditions. No invented entities are introduced.

free parameters (3)
  • Peak-height anatase scaling factor (constant 8 in Eq. 1) = 8 (dimensionless)
    Adopted from Berger-Keller et al. (Ref 40) for plasma-sprayed titania powder; applied to SP-HVOF Nb-doped TiO2 without recalibration.
  • Peak-height rutile scaling factor (constant 13 in Eq. 1) = 13 (dimensionless)
    Adopted from Berger-Keller et al. (Ref 40) for plasma-sprayed titania powder; applied to SP-HVOF Nb-doped TiO2 without recalibration.
  • Peak-area rutile scaling factor (constant 1.265 in Eq. 2) = 1.265 (dimensionless)
    Adopted from Yang et al. (Ref 42) for suspension flame-sprayed nano-TiO2; applied to a different feedstock and process without recalibration.
assumptions (4)
  • domain assumption The simulated gas temperatures for this modified TopGun HVOF system at 85 mm (1880 C at 25 kW, 2480 C at 75 kW) accurately represent the thermal environment experienced by the droplets.
    Values are taken from Ref 43, an in-house numerical study by the same group, with no experimental temperature measurement in this paper. The explanation of particle melting and phase formation depends on these numbers.
  • ad hoc to paper The two spray conditions differ only in flame power; all other deposition parameters are equal and changes in H2/O2 flow rates do not independently affect microstructure or phase.
    Section 2.1 reports different H2 and O2 flow rates (78/182 l/min vs 229/533 l/min) for the two runs, which also change flame velocity, momentum, and chemistry. The paper attributes all observed differences to 'flame power' without establishing single-variable control.
  • domain assumption Rietveld refinement with undoped anatase and rutile ICSD structures yields valid phase fractions for Nb-doped TiO2; Nb-induced lattice expansion only causes a peak shift that can be ignored.
    Section 3.1 states the d101 spacing in anatase increases with Nb substitution and that this shift could not be taken into account. The quantification assumes undoped structural models remain adequate.
  • domain assumption The semi-empirical calibration constants in Equations 1 and 2, derived for plasma-sprayed titania powder and suspension-sprayed nano-TiO2, are valid for SP-HVOF Nb-doped TiO2.
    The constants are applied directly to measured peak heights and areas without recalibration. Crystallite size, stress, or doping shifts could alter the calibration.

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Pith. "Pith review of Splat formation and microstructure of solution precursor thermal sprayed Nb-doped titanium oxide coatings." pith.science (2026). https://pith.science/paper/ALM56AAJ

@misc{pith2026190804669,
  author       = {Pith},
  title        = {Pith review of: Splat formation and microstructure of solution precursor thermal sprayed Nb-doped titanium oxide coatings},
  year         = {2026},
  howpublished = {\url{https://pith.science/paper/ALM56AAJ}},
  note         = {Machine review of arXiv:1908.04669}
}
read the original abstract

Solution precursor thermal spray can become a breakthrough technology for the deposition of coatings with novel chemistries; however, the understanding of the process that the feedstock material undergoes is still poorly understood when compared to more traditional presentations (i.e. powder and suspension). In this paper, niobium-doped TiO2 coatings were deposited by solution precursor high velocity oxy-fuel spraying, studying its microstructure and phase. It was reported that a lower flame temperature produced a highly porous coating, while the porosity was reduced at higher flame temperature. Investigation of the phase content showed that, contrary to our current understanding, a higher flame power implied an increase of the anatase phase content for solution precursor spray. Three methods were used: Rietveld refinement, peak height and peak area of the x-ray diffraction patterns. Additionally, single splats were analysed, showing that as the precursor travels through the flame, pyrolysis and sintering takes place to form the solid material. These results were used to derive a model of the physico-chemical transformation of the solution precursor. This work proves that solution precursor thermal spray is a promising technique for the deposition of doped ceramic coatings, being the microstructure and phase content controllable through the spraying parameters

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Pith tools

Reviewed August 14, 2026 · model on record in the stance chip above.