Nitrogen-vacancy centre formation via local femto-second laser annealing of diamond

Alastair Stacey; Alexander J Healey; Benjamin Cumming; Brant C Gibson; Brett C Johnson; Davin Yue Ming Peng; Hiroshi Abe; Philipp Reineck; Rebecca Griffin; Takeshi Ohshima

REVIEW 2 major objections 5 minor 29 references

Nitrogen-vacancy centre formation via local femto-second laser annealing of diamond

T0 review · 2 major / 5 minor · reviewed 2026-08-06 · deepseek-v4-flash

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Pith's one-line read Femtosecond laser pulses at low energy can locally anneal diamond, making pre-existing vacancies diffuse to nitrogen atoms and form nitrogen-vacancy centres without creating new vacancies.

desk verdict Solid, honest experimental study; the diffusion-regime evidence is real, but the 'no vacancy creation' claim needs qualification because the control misses V- and does not match the irradiated sample. read the letter →

arxiv 2507.18027 v1 pith:W3PDYPZW submitted 2025-07-24 cond-mat.mtrl-sci quant-ph

Davin Yue Ming Peng , Alexander J Healey , Rebecca Griffin , Benjamin Cumming , Hiroshi Abe , Takeshi Ohshima , Alastair Stacey , Brant C Gibson

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Brett C Johnson Philipp Reineck

This is my paper · ORCID

classification cond-mat.mtrl-sciquant-ph

keywords nitrogen-vacancycentresfemtosecondlaserwritingdiamondvacancydiffusionlocalannealingphotoluminescenceODMRquantumdefects

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 tries to establish that femtosecond laser pulses can locally anneal diamond: at low pulse energy (4.5 nJ), the laser's main action is to make pre-existing vacancies diffuse rather than to create new vacancies. The evidence is a long-dwell experiment in an electron-irradiated diamond where the neutral vacancy (GR1) photoluminescence drops while nitrogen-vacancy (NV) photoluminescence rises over up to 32 hours, with no such change in a pristine control. If correct, this gives a way to activate and fine-tune NV centres with micrometre spatial precision and without a bulk high-temperature anneal, which matters for building quantum sensors and photonic devices in diamond.

What carries the argument

The central mechanism is local laser-assisted vacancy diffusion. A 100 fs, 800 nm pulse at 4.5 nJ deposits energy into the diamond lattice without reaching the multi-photon ionisation threshold for vacancy creation; instead it mobilises pre-existing vacancies, which diffuse to substitutional nitrogen and bind into NV centres. The key diagnostics are the anti-correlated photoluminescence signals of the neutral vacancy (V0, GR1 ZPL at 744 nm) and the neutral NV centre (NV0), measured over dwell times up to 32 hours, together with ODMR spectra that show unchanged spin properties below roughly 40 nJ.

What would settle it

Track the V0 ZPL amplitude and the NV-/NV0 ratio during a 4.5 nJ dwell in the electron-irradiated diamond: if the V0 decrease were charge conversion, the NV- to NV0 ratio would rise without a commensurate loss of total vacancy signal. Alternatively, repeat the 32-hour dwell in a pristine diamond that has been nitrogen-doped but never electron-irradiated; any new NV or V0 PL above background would refute the claim that no vacancies are created.

Watch

Extended reading notes

Core claim

The central claim is that fs-laser writing has two separable actions: at higher pulse energies it creates vacancies, and at low pulse energies it diffuses existing vacancies. In the electron-irradiated diamond, pulses of 4.5 nJ over dwell times from minutes to 32 hours monotonically increase NV0 PL while decreasing V0 (GR1) PL, and the pristine as-received diamond shows no NV increase under identical conditions, indicating no new vacancies are formed. The authors conclude that the laser locally anneals the crystal, letting vacancies migrate to substitutional nitrogen to form NV centres without bulk thermal annealing. They additionally show that pulse energies below roughly 40 nJ leave NV spin properties (ODMR linewidth, D and E parameters) essentially unchanged, while energies above this introduce strain and eventually graphitisation.

Load-bearing premise

The no-creation conclusion at 4.5 nJ rests on the pristine-diamond control showing no new NV signal, which presumes that any laser-created vacancy would diffuse to nitrogen and become detectable within the dwell time, and that the falling V0 signal is vacancy loss by diffusion rather than a charge-state switch from V0 to V-.

Editorial extensions

If this is right

NV ensembles can be formed in diamond that already contains vacancies without a bulk anneal, enabling activation of localised regions inside photonic structures or near surfaces where high-temperature processing damages material.
Below the vacancy-creation threshold, defect populations can be tuned continuously: vacancies are slowly consumed and converted to NV centres, with potential to avoid vacancy clustering.
Low pulse energies below about 40 nJ create NV centres whose ODMR linewidth remains 13C-limited, meaning the laser-written centres retain good spin coherence.
The combination of vacancy creation at high energy and vacancy diffusion at low energy could allow a two-step process: write vacancies, then locally anneal them into NV centres with controlled charge state.
The technique operates at ambient lab conditions, offering a simple path to patterned NV activation in diamond devices.

Reading between the lines

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

The dwell-time data imply a diffusion-limited conversion, so the growth kinetics could yield a quantitative vacancy diffusivity; a natural test is to measure the NV formation rate versus temperature or pulse repetition rate.
If the diffusion picture holds, the same local-annealing scheme should work for other vacancy-related colour centres in diamond (for example SiV or GeV) by starting from suitably doped material with pre-existing vacancies.
The short-time V0 depletion that outpaces NV0 growth hints at competing vacancy sinks such as divacancy formation; probing for divacancy-related spectral signatures would test this.
The control experiment assumes comparable laser absorption between pristine and electron-irradiated diamond; a control with identical vacancy density but different nitrogen content would more cleanly separate charge-state effects from true vacancy diffusion.

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Editorial analysis

A structured set of objections, weighed in public.

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

Desk Editor's Note

read the letter

Solid, honest experimental study. The long-dwell experiment (4.5 nJ, up to 32 h) in the electron-irradiated sample is a genuinely new dataset: NV PL rises monotonically, V0 PL falls, the depleted zone expands, and a pristine control shows nothing. That is real evidence for laser-facilitated vacancy diffusion. The headline claim that this is a regime where the laser's main action is to diffuse rather than create vacancies is stated more strongly than the evidence allows. The control confirms no observable NV0, NV-, or V0, but it is blind to V- (the ND1 centre), and the paper concedes this in SI Section VI. In the as-received sample, any laser-generated vacancies would likely be negatively charged and thus invisible to the PL scans. The control also uses a sample with no pre-existing V0, so its 800 nm absorption and local heating differ from the electron-irradiated sample. That means the null result does not fully transfer to the case where diffusion is observed.

What the paper does well: the pulse-energy-to-ODMR-quality map is systematic and clean, the negative control is a standard falsifiable check, and the authors are honest about what they cannot measure (absolute densities, focal depth, V- population). They do not recycle fitted parameters, and prior work by Shimotsuma et al. is cited and extended rather than buried. The slight increase in V0 PL at higher pulse energies in the irradiated sample (but not the as-received) is a nice internal consistency check, though it also points to leftover vacancy production in that regime.

The soft spots are in proportion: the diffusion mechanism is not in doubt, but the exclusivity of the 'diffuse rather than create' regime at 4.5 nJ is not proven. A revision that either softens that claim to 'dominant effect is diffusion, with vacancy creation below our detection limit' or adds V- sensitive measurements would settle it. The conversion efficiency is modest (factor-of-two PL increase) and the practical utility is exploratory, but the local annealing capability near photonic structures is a plausible niche.

Recommendation: send it to peer review. The data are worth refereeing, and the central observation will stand even if the framing needs adjustment. A serious referee can push for the V- control or a more careful claim. Keep it on your reading list if you work on laser writing of defect ensembles. It is a competent, useful addition, not a breakthrough.

Referee Report

2 major / 5 minor

Summary. This manuscript investigates femtosecond-laser writing of nitrogen-vacancy (NV) centres in diamond. In an as-received CVD diamond with ~1 ppm substitutional nitrogen, the authors map NV photoluminescence and ODMR properties versus pulse energy (4–90 nJ), finding efficient NV creation with preserved spin properties below ~40 nJ and increasing strain and graphitization above ~60 nJ. In an electron-irradiated diamond pre-loaded with ~10 ppm neutral vacancies, they examine dwell-time evolution at 4.5 nJ and report a monotonic NV PL increase with a concurrent, spatially expanding V0 PL depletion, which they interpret as laser-assisted vacancy diffusion and NV formation without new vacancy creation. The central claim is that a regime exists where the fs-laser's main action is to diffuse rather than create vacancies. The diffusion evidence is plausible and the measurements are clearly presented, but the no-creation half of the claim is weakened by the control's blindness to negatively charged vacancies and by sample-to-sample differences in 800 nm absorption.

Significance. If fully established, the local annealing capability would be useful for deterministic defect engineering in diamond, particularly for avoiding bulk high-temperature annealing near surfaces. The dwell-time experiment is a clear, falsifiable test with a negative control, and the ODMR data provide a useful map of the pulse-energy window that preserves NV spin properties. The analysis involves no fitted parameters recycled as predictions, and the negative control is a genuine control rather than a circular argument. However, the paper's headline 'diffuse rather than create' claim is an exclusivity claim that requires excluding vacancy creation, and the current PL-based control does not measure the V- charge state. The manuscript is therefore a solid experimental contribution whose strongest conclusion needs to be either rephrased or supplemented by a V--sensitive measurement.

major comments (2)

[SI Section IV; main-text Fig. 5; Conclusion] The conclusion that 4.5 nJ fs-laser irradiation 'does not produce lattice vacancies' (SI Section IV) is not established, because the as-received control measures PL with 532 nm excitation and a 570 nm long-pass filter, which detects NV0, NV-, and V0 but is blind to V- (whose ZPL is near 394 nm). SI Section VI explicitly concedes that 'the V− population, which is not measured in our PL scans' is missing. Since the as-received diamond contains ~1 ppm uncompensated nitrogen, any laser-generated vacancies are expected to be negatively charged, as the authors themselves suggest for high pulse energies in the Conclusion, so a null NV/V0 signal cannot exclude creation of isolated V-. In addition, the as-received sample lacks the ~10 ppm V0 population of the e-irradiated sample and therefore has different 800 nm absorption and local heating, so the null result cannot be transferred quantitatively to the e-irradiated case. The central 'diffuse rather than create' claim should be rephrased as 'no detectable NV/V0 creation' or supported by a V--sensitive measurement.
[Fig. 5; SI Sections V and VI] The interpretation of the V0 PL decrease as physical vacancy loss by diffusion is not unique: the same monotonic decrease is also consistent with V0-to-V- charge-state conversion during laser annealing, since V- is invisible to the 675 nm excitation and 725 nm long-pass detection. The expanding spatial extent of the V0-depleted zone reported in SI Fig. S5 is suggestive of diffusion, but the short-time V0 drop and the lack of a V- measurement leave a charge-state contribution unresolved. The authors should either measure V- (e.g., via absorption or low-temperature PL near 394 nm) or explicitly discuss why charge conversion cannot account for the observed depletion; the current text notes only 'multiple vacancy annihilation processes' and does not address the charge-state alternative.

minor comments (5)

[Section III.A] The statement that 'Fs-laser processing in the as-received sample did not result in a clear V0 PL signal, suggesting that V0 defects were not formed in significant concentrations' should also state in the main text that V- was not measured, rather than leaving this caveat only in SI Section VI.
[SI Fig. S5 caption] The caption contains a duplicated word: 'the area of of V0 PL depletion' should read 'the area of V0 PL depletion'.
[Section III.B heading] The heading uses 'E-irrad.' while the rest of the text uses 'e-irrad.'; please standardize the capitalization.
[Fig. 3(c)–(e)] The definition of ΔE and the factor relating the resonance separation to the strain parameter E should be stated explicitly; as written, 'the parameter E = (f+_off − f−_off)' leaves it ambiguous whether this is the full splitting or half-splitting.
[Section III.B, conversion efficiency paragraph] The N-to-NV conversion estimate is based on a factor-of-two PL increase and assumed as-grown NV/Ns of 0.1–1%; this should be labelled as an order-of-magnitude estimate rather than a quantitative conversion efficiency.

Circularity Check

0 steps flagged · score 1.0 of 10

No significant circularity: the central 'diffuse rather than create' claim rests on an experimental control and independent measurements, with no fitted parameter recycled as a prediction.

full rationale

The paper's argument is experimental rather than derived from a model. The central claim that 4.5 nJ fs-laser pulses diffuse rather than create vacancies is supported by the V0 PL decrease and NV PL increase in the e-irradiated diamond over dwell time (Fig. 5), and by the as-received control showing no NV PL increase (SI Section IV). No fitted parameter is later renamed as a prediction, and no equation defines the output in terms of the input. Self-citations (refs [8], [16], [17]) appear only as background for ion-implantation damage and prior fs-laser writing in other materials; they are not load-bearing for the conclusion. The paper does contain an admitted limitation in SI Section VI: 'the V− population, which is not measured in our PL scans' is missing, which means the as-received control cannot exclude creation of immobile negatively charged vacancies, and the two samples differ in defect content and absorption. This is a genuine experimental-sensitivity concern that weakens the exclusivity of the claimed regime, but it is not circularity: the conclusion is not equivalent to its inputs by construction. The only circularity-relevant observation is that the control's interpretation assumes any created vacancies would become observable NV centres, an assumption the paper itself partially acknowledges; this is a falsifiability issue rather than a self-referential derivation. Overall, the derivation chain is self-contained with respect to external benchmarks, and the minor self-citations do not carry the argument.

Assumptions & free parameters 0 free parameters · 6 assumptions · 0 invented entities

The paper introduces no fitted parameters or invented entities. All conclusions rest on domain assumptions about sample composition, PL-to-concentration proportionality, the validity of a negative control, and the charge state of vacancies; these are listed above.

assumptions (6)

domain assumption The as-received CVD diamond contains approximately 1 ppm substitutional nitrogen and less than 10 ppb NV initially (Element Six estimate).
Used as the baseline for interpreting NV PL increases and for estimating N-to-NV conversion in Sections III.A and III.B.
domain assumption The e-irradiated diamond contains approximately 10 ppm V0 vacancies based on the 2 MeV, 10^18 cm^-2 electron irradiation dose and Ref [24].
This pre-existing vacancy population is the reservoir that the proposed local-annealing regime is claimed to mobilize.
domain assumption PL intensity at 650 nm bandpass is proportional to NV ensemble density, and V0 PL at 725 nm longpass is proportional to V0 density, despite different per-defect brightness.
The paper uses relative PL changes as proxies for defect concentration changes (Fig. 5c), and the authors explicitly caution that per-defect brightness differs.
domain assumption The negative control in the pristine diamond (no NV PL increase after 4.5 nJ dwell) proves that no vacancies are created at this pulse energy.
The control assumes that created vacancies would diffuse to nitrogen and form detectable NV centres in this sample within the dwell time, which presumes the same local heating/mobility as in the e-irradiated sample.
domain assumption The V0 PL decrease in the dwell-time experiment reflects physical loss of vacancies (by diffusion or pairing) rather than V0 to V- charge-state conversion.
The laser could generate free carriers and change vacancy charge states; the paper does not measure V- or the 744 nm ZPL lineshape to exclude this.
domain assumption The 650 nm bandpass filter collects both NV0 and NV- emission, and in the e-irradiated sample the observed NV PL is dominated by NV0.
The paper states only NV0 PL is observed in the e-irradiated diamond (Section II.A) and attributes the Fig. 5 NV increase to NV0 formation.

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Cite this review

Pith. "Pith review of Nitrogen-vacancy centre formation via local femto-second laser annealing of diamond." pith.science (2026). https://pith.science/paper/W3PDYPZW

@misc{pith2026250718027,
  author       = {Pith},
  title        = {Pith review of: Nitrogen-vacancy centre formation via local femto-second laser annealing of diamond},
  year         = {2026},
  howpublished = {\url{https://pith.science/paper/W3PDYPZW}},
  note         = {Machine review of arXiv:2507.18027}
}

read the original abstract

Emerging quantum technologies based on the nitrogen-vacancy (NV) centre in diamond require carefully engineered material with controlled defect density, optimised NV formation processes, and minimal crystal strain. The choice of NV generation technique plays a crucial role in determining the quality and performance of these centres. In this work, we investigate NV centre formation in nitrogen-doped diamond using femtosecond (fs) laser processing. We systematically examine the effect of laser pulse energy on NV production and quality using photoluminescence and optically detected magnetic resonance measurements. We also probe the role of pre-existing lattice defects formed by electron irradiation and consider defect evolution over extended dwell times. Finally, we are able to identify a regime where the main action of the fs-laser is to diffuse rather than create vacancies. This local annealing capability expands the toolkit for tailored NV production and presents opportunities for fine tuning defect populations.

Figures

Figures reproduced from arXiv: 2507.18027 by the authors.

**Figure 2.** (a) A series of selected confocal PL maps of NV fluorescence (650 nm band pass filter) [PITH_FULL_IMAGE:figures/full_fig_p006_2.png] view at source ↗

**Figure 3.** NV− ODMR spectra from fs-laser processed spots with pulse energies of (a) 23.75 nJ and (b) 73.56 nJ. Spectra with solid symbols are background spectra taken in a nearby unprocessed area. The solid black line is a multi-Lorentzian fit. A weak bias magnetic field is applied along one set of NV axes. The change in (c) zero field splitting parameter, D = (f + + f −)/2 and (d) the parameter E = (f + off − f − off) as a f… view at source ↗

Figures from the paper (2 more)

**Figure 4.** Figure 4: (a) Confocal PL maps of the e-irrad. diamond sample measured with a 650 nm band pass [PITH_FULL_IMAGE:figures/full_fig_p009_4.png]

**Figure 5.** Figure 5: A series of PL maps of 4.5 nJ fs-laser processed regions for the dwell times indicated (in [PITH_FULL_IMAGE:figures/full_fig_p010_5.png]

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Pith tools

Reviewed August 6, 2026 · model on record in the stance chip above.

[1] [1]

Rovny, S

J. Rovny, S. Gopalakrishnan, A. C. B. Jayich, P. Maletinsky, E. Demler, and N. P. de Leon, Nanoscale diamond quantum sensors for many-body physics, Nat. Rev. Phys. 6, 753–768 (2024)

work page 2024

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S. Pezzagna and J. Meijer, Quantum computer based on color centers in diamond, Appl. Phys. Rev. 8, 011308 (2021)

2021

[3] [3]

Schmitt, T

S. Schmitt, T. Gefen, F. M. Stürner, T. Unden, G. Wolﬀ, C. Müller, J. Scheuer, B. Naydenov, M. Markham, S. Pezzagna, J. Meijer, I. Schwarz, M. Plenio, A. Retzker, L. P. Mcguinness, and F. Jelezko, Submillihertz magnetic spectroscopy performed with a nanoscale quantum sensor, Science 356, 832 (2017)

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Meijer, T

J. Meijer, T. Vogel, B. Burchard, I. W. Rangelow, L. Bischoﬀ, J. Wrachtrup, M. Domhan, F. Jelezko, W. Schnitzler, S. A. Schulz, K. Singer, and F. Schmidt-Kaler, Concept of deter- ministic single ion doping with sub-nm spatial resolution, Appl. Phys. A 83, 321 (2006)

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