Zirconium carbide (ZrC) is a much-promising material, it has received increased interest recently as an alternative material to silicon carbide (SiC) in nuclear fuel applications1,2, in next-generation nuclear fusion reactors3, and also as an ultra-high-temperature ceramic to be used in ceramic-metal composite heat exchangers in concentrated solar power (CSP) plants4,5.

ZrC (here denoted as ZrCx) is typically non-stoichiometric as it can contain up to 50% of unoccupied carbon sites6,7, it has been found that deviations in the stoichiometry of ZrCx can severely affect its thermal and mechanical properties8,9. Given its potential in high-temperature applications, it is extremely important to define a method that robustly determines its stoichiometry and purity. The purity of ZrCx should always be assessed as the presence of contaminants such as nitrogen or oxygen is detrimental for its performance. For example, if ZrCx is to be used as a nuclear fuel coating in a nuclear reactor, any nitrogen contamination should be avoided due to the production of radioactive 14C from nitrogen 14N inside the reactor10.

There are two common methods for defining the stoichiometry of ZrCx. The first one is to evaluate the C/Zr atomic ratio from the lattice parameter measured by X-ray diffraction (XRD) using the correlation published in Jackson & Lee6. The second one is to quantify through the inert-gas fusion technique the carbon content in ZrCx and calculate the C/Zr atomic ratio assuming that the sample is free from impurities. Both techniques, however, have limitations and when used in standalone approaches can lead to erroneous stoichiometry estimations, as we will proceed to demonstrate later in this paper.

The need for an established robust method to measure the stoichiometry of ZrCx is evident when the relationship between the C/Zr atomic ratio and the lattice parameter is considered. Recently, researchers have published a linear correlation8,11,12 between C/Zr atomic ratio and lattice parameter which is in disagreement with the more established relationship from the 1960s–70s showing a maximum at around C/Zr ~ 0.8313,14,15. A significant spread of data exists between ZrCx lattice parameter and stoichiometry, which is summarized in the book of Shabalin16 and first acknowledged by Mitrokhin et al.15. The disagreement in the trends reported, linear versus nonlinear, makes it difficult to clearly characterize the stoichiometry of ZrCx and therefore link thermophysical properties with ZrCx. One of the main reasons for the significant spread of data reported can be ascribed to the difficulties in controlling phase contamination due to the solubility of oxygen and nitrogen in the ZrCx lattice. Additionally, the presence of oxygen in ZrCx lattice gives birth to the oxycarbide class of compounds where there is a direct substitution of carbon (or a carbon vacancy) by oxygen17,18,19. It is also possible for carbon or oxygen to occupy the octahedral interstitial vacancies of the Zr lattice20,21. The oxycarbide was shown to exhibit the exact same rock salt structure of ZrCx (see the Powder Diffraction File, PDF, 035 078422) with similar23 or smaller cell parameters21. Gendre et al.17 observed that oxycarbides with C/Zr ≥ 0.8, have the same XRD pattern as ZrCx while oxycarbides with C/Zr ≤ 0.7 could instead display some additional zirconia peaks17. If ZrCx exists over a wide range of non-stoichiometry (as shown in the phase diagram of by Fernandez-Guillermet24 and Jackson & Lee6), the oxycarbide, here written as ZrCxOy, is also able to exist in the same range of non-stoichiometry. Due to the similarities between the ZrCx and the ZrCxOy, structures it is challenging to differentiate a pure single phase ZrCx sample from an oxygen or nitrogen contaminated sample.

Recent studies8,11,12,20,25 have shown a linear relationship or polynomial relationships between lattice parameter and C/Zr atomic ratio and it is remarkable that the authors presenting this new correlations were working on either ZrCx8,11,12 or ZrCxOy20,25. Zhou et al.26 discuss the difficulties encountered for the determination of carbon and nitrogen inclusions in ZrCx using XRD and they confirmed the expected usefulness of neutron diffraction to determine accurately carbon and oxygen stoichiometries. However, neutron diffraction could not or was not used for the characterization of ZrCx specimens in other literature8,11,12,13,14,20,25, obviously because this technique is quite difficult to access (only ~20 facilities worldwide having an external users program27). Other techniques such as Raman spectroscopy that could be used to detect the presence of microcrystalline carbon or amorphous carbon in carbide systems28,29, or X-ray photoelectron spectroscopy (XPS) that can also help distinguish the nature of bonds present in the sample, if the metal in the carbide is bonded with carbon, oxygen30 or nitrogen31, are not often used within the ceramic processing community.

This work presents a critical analysis of the stoichiometry of ZrCx as past literature is reassessed depending on the method of sample production, with emphasis on samples manufactured in graphite crucibles or in vacuum and length of heat treatment used. It is found that the linear relationship between the lattice parameter and the ratio C/Zr recently reported on ZrCx12 samples is erroneous as the samples analysed in these studies were ZrCxOy and not ZrCx due to a lack of in-depth characterization.

Additionally, the stoichiometries of hot pressed ZrCx samples manufactured using commercial powder have been analysed with 3 independent experimental techniques demonstrating that nuclear magnetic resonance (NMR) can detect the presence of graphite when XRD cannot. The comparison of stoichiometry obtained with the three techniques on the same samples elucidates the uncertainty in the stoichiometry definition of ZrCx in past and recent literature and provides recommendation for the use of our proposed standardized method for the evaluation of the stoichiometry of ZrCx in future studies.

Experimental Procedure

Sample preparation and characterization

Hot pressed ZrCx samples were manufactured using ZrC commercial powder (3–5 μm, 90% <8 μm with contamination of 0.2% <hafnium <2%, Grade B, H.C. Starck, Karlsruhe, Germany) using the procedure previously described in our previous work32 where Set A and B refer to samples hot pressed at 1850 °C and 2000 °C respectively. Set A was made using approximately 42 g of ZrC powder in a 40 mm graphite die, the height was about 0.5 cm. Set B was made using 85 g of ZrC powder filled in the same die, the final height of the disc was 1 cm. The die was lined with graphite foil before powder was inserted to facilitate extraction of the sample. The heating procedure, in argon atmosphere, was set in stages: first heating to 600 °C then a ramp of 20 °C/min was used to reach 1800 °C. A third ramp of 10 °C/min was used to reach the final desired temperature of 1850 °C or 2000 °C. After the desired temperature was reached, samples were hot pressed for 1 h after the 50 MPa of uniaxial pressure was completely applied (it took approximately 15 min). The density was measured with Archimedes method on machined samples cut by electrical discharge machining (EDM) method. To compare the density values obtained with the Archimedes method on different samples tested, the percentage of the theoretical density, TD, was here reported. The TD considered for ZrC was 6.63 g/cm3. The density results for Set A and Set B samples are reported in Table 1. Two Set B samples were manufactured using the same powder and same hot pressing procedure and the results from analysis of these two bulk samples are reported.

Table 1 Set A and Set B hot pressed samples density results. Measurements were calculated on machined samples cut from bulk discs.

Sample lattice parameters were calculated using XRD characterization with a Bruker D2 Desktop (Massachusetts, USA), with a copper Kα source. XRD was performed in the range 2θ: 20–90°. WinPLOTR (Fullprof suite software33,34) was used for XRD pattern refinement using Le Bail method and Rietveld refinement. Rietveld refinement cannot be used to obtain information of carbon, oxygen and nitrogen site occupancy due to the fact that XRD data are dominated by the scattering of the cation sublattice, Zr26. However, both methods were used to calculate ZrCx lattice parameter: the same value was obtained from either Le Bail or Rietveld refinement, nonetheless, Rietveld refinement reduced uncertainties. Sample grain sizes were observed using channelling contrast in a scanning electron microscopy (SEM) using backscattered electron images (BSEI) with a LEO Gemini 1525 FEG-SEM, Zeiss, Germany. Sample surfaces were polished using a Struers MD-Piano cloths 2000 and 4000 grit followed by a 1 µm diamond solution applied on a Struers MD Dac cloth.

Stoichiometry techniques

The stoichiometry (C/Zr atomic ratio) of samples from Set A and Set B was analysed using three approaches:

  1. 1.

    C/Zr atomic ratio was obtained by fitting the lattice parameter calculated from XRD refinement with the trendline reported in Jackson & Lee6 for impurity-free ZrC samples;

  2. 2.

    ZrCx stoichiometry was calculated using the full combustion technique in a thermogravimetric analyser coupled with a differential thermal analyser (TGA/DTA);

  3. 3.

    Carbon content in weight % was measured using a carbon analyser and this was subsequently converted into atomic % for definition of C/Zr atomic ratio. NMR was then used to correct C/Zr atomic ratio when inconsistencies were found with results from methods 1 and 2.

Full combustion method (TGA/DTA)

The full combustion technique using a thermogravimetric analyser coupled with a differential thermal analyser (TGA/DTA) was performed in isotherm mode using a Netzsch STA 449F1 (Netzsch, Germany). A sample from Set A or Set B, previously machined by EDM, was inserted in a TGA/DTA and heated to 1200 °C for Set A and to 1000 °C or 1100 °C for Set B with a rate of 10 °C/min under an argon atmosphere (60 mL/min of argon flow). When the temperature was reached, the sample was kept under argon atmosphere for 20 min to allow the temperature to stabilize before switching to air. The air flow was set to 60 mL/min and the exposure to the oxidizing environment was kept constant for 5 hr or 2 hr and full combustion was reached after approximately 1 hr. The initial mass of the sample, expressed in weight %, here %mZrC, and the final mass of the sample, here %mZrO2, were recorded. To avoid any possible mass change due to buoyancy affected by gas flow rate insertion, both the argon and air fluxes were set to 60 mL/min. The oxidation of ZrCx was considered to follow the reaction:


where all carbon is converted to CO2. From the mass gain evaluated via TGA it was possible to calculate the mass of the final sample by using:

$${m}_{{\rm{final}}}=\frac{{m}_{{\rm{ZrC}}}\,\cdot \% {m}_{{\rm{ZrO}}2}}{ \% {m}_{{\rm{ZrC}}}}$$

where mZrC is the initial sample mass measured before the experiment, %mZrO2 and %mZrC are mass percentages (weight %) obtained from TGA analysis. After calculating the final mass of the sample, which is considered to be zirconia, mfinal, as all carbon is converted to CO2 via Eq. 1, it is possible to derive the mass of zirconium in ZrO2 using:

$${m}_{{\rm{Zr}}-{\rm{in}}-{{\rm{ZrO}}}_{2}}={m}_{{\rm{Zr}}-{\rm{in}}-{\rm{ZrC}}}=\frac{{m}_{{\rm{final}}}\,\cdot M{W}_{{\rm{Zr}}}}{M{W}_{{{\rm{ZrO}}}_{2}}}$$

where MW is the molecular weight of Zr (91.224 g/mol) and of ZrO2 (123.218 g/mol). The mass of carbon present in the initial sample is calculated from:


These equations consider that the samples are not contaminated by secondary phases or contaminants. After these calculations, the C/Zr ratio was calculated from:


The uncertainty on the reported value of C/Zr atomic ratio is the standard deviation obtained by performing three calculations using different steady states points for %mZrC and %mZrO2.

Inert gas fusion

Stoichiometry of Set A and Set B was reassessed using an inert gas fusion technique, also called carbon, nitrogen, oxygen analysers using an EMIA 320 V2 and EMGA 820 from Horiba Scientific (Horiba, Japan). This widely used technique allows the quantification of all carbon species present in the ZrCx samples but without the possibility of discriminate between bonded carbon (e.g., ZrC) or free carbon (amorphous carbon or graphite). Carbon content in ZrCx samples from Set A and Set B was compared to the carbon content present in the commercial powder used. ZrC commercial powder has, according to the manufacturer, a carbon content of 11.6 wt% (11.1% being combined and 0.5% being free carbon). The ZrC commercial powder analysed with the equipment used for this study showed a carbon content of 11.7 ± 0.1 wt%35, in line with the manufacturers’ specifications. As described in our previous work35 the hot pressed ZrCx pellets from Set A had a carbon content of 11.2 ± 0.1 wt%, while pellets from Set B had a carbon content of 11.9 ± 0.1 wt%. The stoichiometry of Set A and Set B from elemental analysis was reported as all other impurities were measured (oxygen and nitrogen) and an accurate (global) C/Zr atomic ratio could be estimated. A small amount of sample, with a mass of approximately 15–70 mg, was used for each measurement. All the uncertainties reported have been calculated as the standard deviation based on 3 measurements.

Nuclear magnetic resonance (NMR)

Solid-state static 13C nuclear magnetic resonance (NMR) spectroscopy was performed on Set B at room temperature to investigate the distribution of carbon environments within the sample and reassess the quantity of carbon bonded in ZrCx. As ZrCx is semi-metallic, shielding from the radiofrequency (RF) waves generated by the NMR can occur if the powder particle diameter is above the skin depth (~33 μm) of the sample. The sample was initially broken using a hammer and further reduction in particle size was achieved using a planetary ball miller (Deco Equipment, China) with stainless steel pots and agate milling balls. The samples were milled until they could be filtered through a 25 µm sieve. The powdered samples were loaded into a 7.5 mm zirconia NMR rotor with aluminium nitride spacers. Static room temperature NMR spectroscopy was undertaken on a Varian Infinity spectrometer at a frequency of 100.603 MHz, for 13C NMR in a 9.4 T magnet. The 13C NMR spectra were referenced to tetramethylsilane (TMS) via a secondary reference to solid adamantane. Sample spectra were obtained using a Hahn echo pulse sequence, typically around 10000 acquisitions were acquired with a π/2 of 4.70 μs pulse and a pulse delay time of 9 s which were determined to be non-saturating conditions. Peak fitting was undertaken using a Voigt profile, and the Chi squared value was minimized using the Levenberg-Marquardt algorithm in Igor Pro software (WaveMetrics, 10200 SW Nimbus, G-7 Portland, OR 97223, USA). Graphite powder (282863 Sigma-Aldrich, <20 μm, synthetic, purchased from Aldrich Chemistry, Sigma-Aldrich, Merck, Darmstadt, Germany) was used to calibrate the graphite peak observed during analysis of Set B samples, no sample preparation was needed in this case.


BSEI revealed the grain size and level of porosity of Set A and Set B samples (shown in Fig. 1). The grain size of samples hot-pressed at 1850 °C was smaller than the grain size of samples hot-pressed at 2000 °C. Additionally, samples hot-pressed at 2000 °C (Set B) showed less porosity than samples hot-pressed at 1850 °C (Set A) as can be seen by comparing Fig. 1a,b.

Figure 1
figure 1

BSEIs of: (a) Set A sample showing a TD of 96.5%; and (b) and Set B sample showing a TD of 99.2%. Grain microstructure is shown by channelling contrast.

According to the XRD analysis shown in Fig. 2, in the limit of sensitivity of the XRD apparatus, both Set A and B samples did not display any secondary phase rich in oxygen (such as ZrO2) or graphite. Set A showed a carbon content of 11.2 ± 0.1 wt% in line with the combined carbon concentration in the initial ZrC powder. Set B, however, showed a carbon content of 11.9 ± 0.1 wt% indicating the presence of additional free carbon or graphite picked up during the hot pressing stage as commercial ZrC powder only contained 11.6 wt% of bonded and free carbon.

Figure 2
figure 2

XRD Set A and Set B samples showing ZrC diffraction peaks (PDF 035 0784), no secondary phases were detected.

The nature of the additional presence of carbon measured by inert gas fusion carbon analysis associated with Set B samples could be detected using NMR as this technique can distinguish different carbon local environments. In 13C NMR carbon atoms can be directly observed, the integration of a spectral peak corresponds to the proportion of carbon atoms in the associated unique bonding environment and ratio of this with the total spectral signal corresponds to the fraction of carbons present in that environment. NMR was used to analyse the nature of carbon in one Set B sample, the results are shown in Fig. 3.

Figure 3
figure 3

Static 13C NMR spectra at room temperature of: (i) Set B sample in red, ZrC peak fit (blue) and baseline (green); (ii) the residual spectrum post-fitting; and (iii) graphite powder. Common peak positions are highlighted with a vertical grey line for comparison.

The static 13C NMR spectrum at room temperature in Fig. 3(i) shows that two narrow resonances are observed in Set B sample. The ZrCx and graphite resonances are located at ~437 and 113 ppm, respectively. Peak fitting was undertaken on the spectra for the ZrCx resonance and it is shown in blue in Fig. 3(i). The post-fit residual spectrum of Fig. 3(i) is shown in Fig. 3(ii). The attribution of graphite to the lower shift resonance, 113 ppm, was confirmed by undertaking static 13C NMR of a graphite powder, this is shown in Fig. 3(iii). The separation of the broad line shape of the ZrCx and the graphite resonances indicate that graphite present in the sample is entirely disassociated with ZrCx structure. The line shape of the ZrCx resonance structure, as determined by static 13C NMR is homogeneous with no additional sub-resonances. The homogeneity of the ZrCx resonance observed in the static spectra is indicative of a single unique carbon chemical environment associated with the ZrCx phase. NMR analysis enabled discrimination between carbon in ZrCx and carbon disassociated from the ZrCx structure which in turn made it possible to recalculate the proportion of carbon atoms in the ZrCx sites and hence redetermine the stoichiometry of the sample. By comparing the fitted peak area of the graphite resonance with the total peak area of the NMR spectrum it was possible to correct the C/Zr ratio of ZrCx previously calculated by elemental carbon analysis. Static 13C NMR on Set A was also undertaken and showed presence of the graphite peak at 113 ppm. Corrected values of stoichiometry for Set A after NMR analysis were also performed and these are discussed in Table 2.

Table 2 Summary of hot pressed ZrC samples stoichiometry.

TGA/DTA was used to estimate the stoichiometry of Set A and Set B samples using the full combustion method, shown in Fig. 4. The TGA data were used to measure samples stoichiometry by using Eqs. 25.

Figure 4
figure 4

TGA/DTA data obtained during full combustion: (a) Set A sample at 1200 °C; (b) and (c) Set B samples at 1100 °C and 1000 °C, respectively.

The broad DTA peak in Fig. 4a–c was considered to be related to ZrC oxidation as it coexisted with the TGA curve.

A summary of the stoichiometry results obtained independently from TGA analysis, carbon analysis and NMR analysis are reported in Table 2. The total carbon content of Set B sample, measured by carbon analysis was found to be related to a C/Zr =1.02 ± 0.01, by applying post NMR correction and subtracting the amount of graphite detected in the sample (shown in Fig. 3), the amount of bonded carbon was measured to be related to a stoichiometry of C/Zr = 0.96 ± 0.01 in Set B sample, in agreement with the stoichiometry measured with TGA analysis in Table 2.

Set A stoichiometry value obtained by elemental analysis and TGA was in agreement: C/Zr ratio = 0.97. The mass increase measured by TGA and shown in Fig. 4a indicated a C/Zr value of 0.97 ± 0.01. If oxygen and nitrogen quantities were not considered for the stoichiometry calculation, then C/Zr would have been 0.96 ± 0.01, this indicates the importance of measuring all contaminants when reporting ZrCx stoichiometry. When the nitrogen and oxygen elemental analyses on Set A and Set B are considered, these specimens should actually be labelled as an oxynitrocarbides. Only by measuring all contaminants the sample stoichiometry can be determined: Set A, for example has a considerable presence of oxygen and nitrogen and should be labelled ZrC0.97O0.06N0.02.

Another issue occurring when contaminants are not fully quantified is that sample stoichiometry may be erroneously determined using the correlation in Jackson & Lee6 for pure ZrC samples. If the correlation in Jackson & Lee6 for pure ZrC samples is used on Set A, the stoichiometry is C/Zr = 0.575, a highly substoichiometric sample which is in disagreement with all experimental measurements shown in Table 2. To understand the discrepancy between the C/Zr measured experimentally by TGA and carbon analysis and the fitted C/Zr atomic ratio in Jackson & Lee6 from lattice parameter, the relationship between lattice parameter and impurity contents that was first published by Mitrokhin et al.15. was analysed. The Mitrokhin et al.15. equation, which was then republished by Jackson & Lee6 and Shabalin16, is:


where x corresponds to C/Zr and y is (O + N)/Zr. This equation is only applicable when 0.62 ≤ x ≤ 1 and y ≤ 0.3, as reported by Mitrokhin et al.15., therefore it should not be used for C/Zr <0.62 sub-stoichiometric samples.

The stoichiometry of Set A sample, showing a lattice parameter of a = 4.6920 Å ± 0.0001, was reanalysed using Eq. 6 considering the boundary condition reported by Mitrokhin et al.15. and adding the constraint of x + y = 1 for stoichiometric compounds. The result is that Set A could appear as an oxycarbide with a stoichiometry of ZrC0.88O0.12 (x = 0.88 and y = 0.12). This value, ZrC0.88O0.12, is still in disagreement with the stoichiometry evaluated by TGA and carbon analysis, ZrC0.97, see Table 2. The oxycarbide value of ZrC0.88O0.12 evaluated for Set A using Eq. 6 is, however, not the only possible solution for that given lattice parameter as ZrCx allows for non-stoichiometric compounds, therefore ZrC0.85O0.10 could also be possible. A representation of the quadratic Eq. 6 which covers all possible oxycarbide stoichiometries is highlighted in Fig. 5a,b. The upper limit of the Mitrokhin et al.15. equation is superimposed upon the experimental data of lattice parameter versus C/Zr from old literature (1960s-1970s)13,14, recent literature8,11,12,17,20,26,36,37 and the experimental data presented in this work. Figure 5 deliberately combines experimental data from zirconium carbide ZrCx8,11,12,13,14,26,36,37,38 and oxycarbide ZrCxOy17,20,21,38 studies.

Figure 5
figure 5

(a) Lattice parameter against C/Zr ratio showing Mitrokhin et al.15 fit, Nakayama et al.12 fit and Réjasse et al.20 fit superimposed on zirconium carbide and oxycarbide experimental data, references are in square brackets and H.T. stands for heat treatment. (b) Mitrokhin et al.15 equation plotted over the same range shown in (a) with varying oxygen and nitrogen contents: 0 ≤ y ≤ 0.3. (c) Close-up of the lattice parameter against C/Zr presented in this work shown in (a) using three different experimental techniques: TGA, carbon analyser and NMR. Lattice parameter of Nachiappan et al.11 samples increased after heat treatment as highlighted by the arrow and the “heat treatment” caption.

Recent data on oxycarbide production were not reported in Fig. 5 as their stoichiometry was not defined independently but was derived from pre-existing data. Hauser et al.25. samples stoichiometry, for example, was estimated by fitting their lattice parameter over pre-existing oxycarbide values from Gendre et al.17, Barnier et al.21 and Constant et al.39. The oxycarbide stoichiometry data reported in Gendre et al.17, Barnier et al.21 and Constant et al.39 are in agreement with the equation reported by Mitrokhin et al.15 for the Zr-C system for y ≠ 0.


There is an evident discrepancy in the relationship between lattice parameter and C/Zr ratio in the literature reported from the 1960s and 1970s13,14, that shows a peak of the former at a value of C/Zr ~ 0.8313,14, and the linear or polynomial correlations found in recent literature8,11,12,17,20, which mostly focuses on zirconium carbide ZrCx or oxycarbide ZrCxOy, production and characterization.

By comparing the experimental method reported in Sara13, Storms & Wagner14 and Mitrokhin et al.15, it was noticed that long heat treatments (up to 160 hr) and high temperatures (up to 3300 °C) were used for the production of nonstoichiometric ZrCx. Storms & Wagner14, for example, sintered the powders at 2727 °C before treatment in either vacuum or graphite (at 1325–2050 °C) over long periods (from 1.2 to 160 hr). Mitrokhin et al.15 reported hot pressing ZrC0.96 and ZrH2 at 2600 °C for 30 min followed by heat treatment at 2700 °C for 5 hr to obtain non-stoichiometric ZrCx. Sara13 prepared ZrCx samples using heat treatments at 2600 °C or 3300 °C for a few hr.

By comparing data reported by Storms & Wagner14, shown in Fig. 5a, it became evident that samples that are heat treated in graphite (for 15 hr to 160 hr at temperatures in the range 1775–2000 °C) and samples heat treated in vacuum (for 1.2 to 15 hr at temperatures in the range 1325–2500 °C) can show similar C/Zr versus lattice parameter relationships. The samples heated in graphite may present carbon contamination due to the diffusion of this species in the carbide during heat treatment, especially considering the very long hot-pressing stage in graphite (between 15 hr and 160 hr). Storms & Wagner14 did mention that two of the graphite heat treated samples contained free carbon. One key point emerging from the manufacturing process of Storms & Wagner14 and Sara13 is that very low oxygen contents were reported on the final ZrCx samples with stoichiometries in the range 0.648 < x < 0.985. The oxygen concentration reported in Storms & Wagner14 for ZrCx samples ranged between 148 to 1300 ppm which converted in weight% is equal to 0.0148 wt% and 0.13 wt%.

In this work, oxygen impurities reported in ZrCx samples from past studies13,14 are compared to oxygen impurities reported in recent literature12,26 (even though very few authors reported oxygen concentration measurements). It is found that oxygen contamination from current manufacturing routes is much higher than in the 1960s-70s13,14. We reassessed the reported stoichiometry of recently manufactured ZrCx compounds by taking into account, when published, the oxygen contamination. We found that what was published as ZrCx compounds should have been called, instead, ZrCxOy, an oxycarbide. The reassessment of samples stoichiometry from previous studies12,26 is shown in Table 3. The samples stoichiometry in Table 3 was calculated converting the reported elemental analysis measured in weight % with atomic % and assuming that no vacancies are present, i.e. the sum of x and y in ZrCxOy is equal to 1. For comparison, samples with similar stoichiometry from Storms & Wagner14 are reported to show that Storms & Wagner14 produced pure ZrCx compounds. Unfortunately, other authors8,11,40 recently reporting linear relationship between C/Zr and ZrCx lattice parameter have not reported any oxygen and nitrogen analysis on their samples. It is therefore not possible to discern whether their samples were ZrCx or ZrCxOyNz. Wei et al.8 did mention that the discrepancy of their measurements compared to Sara13 and Storms & Wagner14 could have been induced by presence of impurities such as oxygen but they did not quantify them.

Table 3 Corrected stoichiometry from recent studies, the samples when are reassessed to be oxycarbides instead of carbides have been renamed.

Even though Zhou et al.26 reported that carbon stoichiometry increased and dissolved oxygen decreased with increasing synthesis temperature from 1300 °C to 2000 °C, they reported all their compounds to be ZrCx even though they showed a significant level of oxygen even at 2000 °C (see Table 3). From our analysis shown in Table 3 the level of oxygen present in Zhou et al.26 and Nakayama et al.12 ZrCx samples are of the same order of magnitude of Réjasse et al.20 oxycarbide samples. We, therefore, renamed Zhou et al.26 and Nakayama et al.12 samples oxycarbide compounds, ZrCxOy, as shown in Table 3 due to their level of oxygen contamination.

The very long heat treatments and high temperatures used in past manufacturing processes13,14,15 are considered the reason for the high purity ZrC samples synthetized in the 1960s and 1970s13,14.

It is worth noting that one of the experimental methods widely used to quantify oxygen content in carbide systems is the inert gas fusion or combustion method technique. In this technique the sample sits in a graphite crucible and is heated to very high temperatures in a helium gas atmosphere to burn all oxygen contaminants into CO/CO2. The very long heat treatments in graphite or vacuum at high temperatures conducted by Sara13 and Storms & Wagner14 may have acted in the same way as the inert gas fusion technique: temperature and time allowed conversion of most of the oxygen in contact with free carbon or graphite to escape the system as CO/CO2 leading to oxygen free ZrCx samples. These authors13,14 both found a relationship between the lattice parameter and ratio C/Zr that exhibited a maximum at ~ 0.83 and this was recently confirmed by Mellan et al.41. Mellan et al.41 reported the lattice parameter of ZrCx to decrease from x = 0.97 to x = 1 using computational calculations, as the volume of vacant carbon site (in sub-stoichiometric ZrCx compounds) is larger than the corresponding volume of the perfect crystal. This means that the lattice parameter should expand, or increase, for x < 1.

The assessment conducted in this work proves that past studies13,14,15 are the only ones that reported production of pure zirconium carbide compounds with very little oxygen impurity, less than 1300 ppm, (we excluded in our discussions one sample reported in Storms & Wagner14 that contained 8100 ppm of oxygen with an abnormal lattice parameter of 4.7149, visible as an outlier point in Fig. 5a). The linear relationship found in recent work8,11,12 between C/Zr and lattice parameter was derived in studies where the samples instead of being ZrCx12,26 were, unintentionally, oxycarbides: ZrCxOy, as seen in Table 3. The presence, or contamination, of oxygen in ZrCx samples produced using commercial ZrC powder like in Nakayama et al.12 work and this work (see, for example, Set A oxygen and nitrogen analysis in Table 2 relating to ZrC0.97O0.06N0.02) or by mixing ZrH2 and carbon black26 could be related to the manufacturing process used nowadays, which is shorter (less than 5 hr8,11,26 or even only a few min12,36) and conducted at lower temperatures (≤ 2100 °C) than the manufacturing process used in the past (up to 160 hr14 and 3300 °C13). The combination of short reaction and sintering time combined with low temperatures have induced production of contaminated ZrCx samples hosting oxygen impurities, therefore being in reality oxycarbides.

Before considering changes in mechanical and physical properties of ZrCx with stoichiometry, samples should be correctly characterized, and the stoichiometry be accurately reported considering oxygen and nitrogen contamination. This will help reducing the large scatter of data present to date on thermophysical properties of ZrCx.

Our study showed that the trend reported by Mitrokhin et al.15 and republished in Jackson & Lee6 for pure ZrC, is no longer able to represent the experimental data reported in recent studies8,11,12 (see Fig. 5a). The reason was not related to a novel linear relationship of the lattice parameter with C/Zr atomic ratio recently reported but, instead, was due to the erroneous labelling of samples stoichiometry: recent literature who reported ZrCx have unintentionally produced oxycarbides12,26 instead of carbides (see Table 3).

The increase of lattice parameter of ZrCx samples after post heat treatment reported by Nachiappan et al.11 agrees well with our hypothesis that ZrCx samples manufactured nowadays contain contaminants. It is well known that the lattice parameter of oxycarbides increases with the progressive removal of oxygen21, therefore, by heat treating samples in Nachiappan et al.11 study, most of the oxygen contaminants could leave the system as CO/CO2. In Fig. 5c it was highlighted the change in lattice parameter of heat treated samples from Nachiappan et al.11 that did not quantify the presence of contaminants in their samples. After the heat treatment, their samples presented similar lattice parameter to stoichiometric samples from Storms & Wagner14 which indicated a purification process during heat treatment.

In this work we have used three experimental techniques to measure the stoichiometry of commercial ZrCx hot pressed samples, which contain oxygen and nitrogen contaminations, in an effort to find the best method: TGA, inert gas fusion and NMR. TGA and carbon analysis C/Zr atomic ratio were in agreement on Set A samples even though TGA was unable to measure small levels of impurities such as free carbon and oxygen. Set B samples presented significant non bonded carbon as C/Zr = 1.02 ± 0.01 measured by inert gas fusion analysis and the stoichiometry measured by TGA giving C/Zr = 0.95 ± 0.01 disagreed. NMR was used in this case to quantify the amount of graphite in the sample and to correct the C/Zr ratio. The NMR corrected value of C/Zr = 0.96 ± 0.01 was in agreement with the TGA method for both Set A and set B samples.

We have found that to have a clear understanding of sample stoichiometry in ZrCx systems multiple techniques should be used together, and the relationship between C/Zr atomic ratio and lattice parameter published by Mitrokhin et al.15 and Jackson & Lee6 should be used only if the concentration of carbon, oxygen or nitrogen is known. We propose a method to address stoichiometry of ZrCx in light of the results from this work and the review on past and recent literature, this is shown in Fig. 6.

Figure 6
figure 6

Proposed method to assess ZrC stoichiometry.

In order to evaluate the stoichiometry of a ZrCx sample correctly, we propose the following steps:

  1. 1.

    An elemental carbon, oxygen and nitrogen analysis needs to be conducted and the weight % must be converted to an atomic % to determine whether carbides or oxynitrocarbides are present.

  2. 2.

    TGA can be used as a reliable method to determine the stoichiometry of carbides if the sample is mostly single phase (ZrCx) or if secondary phases are known (e.g., composition of ZrO2).

  3. 3.

    NMR needs to be conducted when discrepancies arise between elemental analysis and TGA analysis. NMR allows correction of stoichiometry from elemental analysis as free carbon or graphite can be identified and quantified.

  4. 4.

    Finally, a comparison between the lattice parameter value obtained by XRD and the relationship published by Mitrokhin et al.15 equation should be performed to validate this theory.

Additionally, we suggest that long heat treatments at high temperature should be used to manufacture pure ZrCx samples as the temperature and time seem to be keys in reducing any remaining oxygen contaminants. Lastly, care should be used when storing and handling carbides powders in air during sample preparation as oxygen contamination is difficult to avoid.


This paper critically analysed the relationship between the atomic ratio C/Zr and the lattice parameter of ZrCx samples. It was found that recent literature reporting on a new linear relationship between these two parameters erroneously did not consider contamination of oxygen and nitrogen in the ZrCx samples under investigation. We reassessed, where possible (i.e., when the quantification of contaminants was reported), the stoichiometry of ZrCx samples that reported a linear relationship between the ratio C/Zr and the lattice parameter and found that those samples were actually ZrCxOy. Additionally, it was noticed that very little oxygen contamination was found in older literature concerning ZrCx due to the specific manufacturing routes that consisted of very long heat treatments (up to 160 hr) at high temperatures (up to 3300 °C), unlike the manufacturing methods used more recently.

The relationship of the atomic ratio C/Zr and the lattice parameter is not trivial and it is not possible yet to define a single and universal technique which is able to characterize the stoichiometry of ZrCx and ZrCxOyNz in one single stage. In our study, we used three independent experimental techniques to identify consistent values for ZrCx stoichiometry. If each method was used alone, instead, a scatter on the atomic ratio as high as ΔC/Zr = 0.07 were found. From this work, we established that a chemical quantification of the carbon, oxygen and nitrogen contents should always be conducted, and the results should be compared with the TGA method which was found reliable in confirming the stoichiometry obtained by elemental analysis. In the case of a discrepancy between TGA and elemental analysis, NMR should be used to correct the final stoichiometry, and the oxide from TGA analysis should be analysed to confirm presence of non-combusted carbon species (as shown in the Supplementary Information).

It is clear that a standardized procedure should be established in order to allow reliable comparisons between stoichiometry and the mechanical and thermophysical properties of ZrCx. We hope that our proposed method will help future researchers to fully and accurately characterize sample stoichiometries and link these data to other physical or chemical material properties.