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ABSTRACT Measuring temperatures during high-temperature processing of steels is usually limited to surface measurements that cannot directly assess the internal temperature distribution.

Here, we demonstrate the feasibility of using a magnetic flux density measurement system to assess transient and non-homogeneous temperature fields in a modern high-strength steel, within

the intercritical temperature range where microstructural evolution defines their key mechanical properties. The system accurately detects the Curie temperature and distinguishes temperature

change rates within the processed volume. The magnetic measurements are also sensitive to the volume above Curie temperature and its shape, as revealed when integrated with thermal

computational simulations. The electromagnetic signal provides real-time qualitative and quantitative information relevant to the metallurgical conditions enabling future intelligent control

systems for the production and processing of steels. Contactless measurements of temperature-dependent electromagnetic properties can enable through-thickness temperature monitoring

solutions, opening up opportunities for non-destructive full-field imaging of steels during thermal and thermomechanical processing. SIMILAR CONTENT BEING VIEWED BY OTHERS RESEARCH AND

APPLICATION OF MULTI-FREQUENCY ELECTROMAGNETIC TECHNOLOGY IN REAL-TIME ONLINE CHARACTERIZATION OF STEEL MICROSTRUCTURES AND MECHANICAL PROPERTIES Article Open access 02 January 2025

_IN-OPERANDO_ ANALYSIS OF THE CORROSION PATTERNS AND RATES UNDER MAGNETIC FIELDS USING METALLIC FILM Article Open access 24 March 2022 IN-SITU 3D TEMPERATURE FIELD MODELING AND

CHARACTERIZATION USING EDDY CURRENT FOR METAL ADDITIVE MANUFACTURING PROCESS MONITORING Article Open access 22 March 2025 INTRODUCTION Today, temperature measurements during high-temperature

processing of steels are limited to surface measurements and cannot directly assess the internal temperature distribution. Measurements of the electromagnetic properties are used in

material characterization but mostly in isothermal and homogenous conditions. However, since the electromagnetic properties of steels are temperature-dependent they can be used to develop

new solutions for contactless, non-destructive, temperature monitoring during high-temperature thermal and thermomechanical processing. Steel is the most important engineering material used

worldwide, hence any small increment in quality and energy efficiency during processing is significantly amplified, resulting in global benefits on economic, environmental and social impact.

Nowadays, modern high-strength steels (HSS) offer superior mechanical properties, which enable leaner, lighter and, therefore, more cost-efficient applications. These steels are typically

produced via thermomechanical controlled processing (TMCP)1, a production route that combines controlled rolling and fast cooling to generate the refined microstructure responsible for the

high-strength alongside good toughness2,3,4. Controlling the temperatures during the final TMCP steps is crucial and the role of the intercritical temperature range, between A1 and A3, is

particularly relevant5,6,7,8. Thermal and thermomechanical processing in this temperature domain promotes the microstructure transformation and grain refinement that are responsible for the

enhanced mechanical properties9,10. Frequently, the application of these steels in the fabrication of structures and components requires some form of joining, typically welding. The

sensitivity of the HSS to the high peak temperatures and cooling rates is well established for the widely used fusion welding methods11,12, including the destruction of the original

microstructure and subsequent degradation of strength, toughness and fatigue life13. Solid-state thermomechanical welding processes, such as Friction Stir Welding (FSW), can overcome this

limitation14. FSW of steel can be performed with peak temperatures inside the [A1, A3] range resulting in fine-grained microstructures with mechanical properties that match or even surpass

those of the original base materials15,16,17. Reliable monitoring, both during production of the raw material and in any subsequent thermomechanical processing operation, can support

intelligent control methods that will prevent the severe microstructure degradation occurring above the A3 temperature, and deliver better material properties18,19,20. There are several

methods for measuring temperatures but most are limited to laboratory applications and/or are not suited for high temperature industrial applications21. Typically, in industrial processes,

temperatures are measured using thermocouples and pyrometers22 or infrared cameras13,23. The former are cumbersome since they require contact and only provide point measurements and the

latter are expensive and quite dependent on surface conditions making it difficult to maintain calibration. Furthermore, both are limited to surface temperature measurements and cannot

directly assess the internal temperature, which is critical when a significant in-depth temperature gradient exists or when the heat is generated internally, e.g. via plastic deformation or

oxidation. Thus, there is a need for advanced temperature monitoring solutions, with a fast acquisition rate, enabling high-speed processing and through thickness assessment. The critical

temperatures associated with phase transformations can be identified indirectly with dilatometry measurements24,25. Differential scanning calorimetry (DSC) can also be used with the added

benefit of detecting the ferromagnetic ↔ paramagnetic transformation at the Curie temperature, TC26,27,28. The electromagnetic properties of steel are directly related to microstructure. In

isothermal conditions, electromagnetic measurements are used to study phase fraction29,30,31, hardness32,33,34, stress-states35,36,37, mechanical properties38, and surface

treatments39,40,41. However, the temperature dependence of the electromagnetic properties42,43 can be further exploited to characterize and monitor the steels during transient thermal and

thermomechanical processing44,45,46 with non-homogeneous conditions. We developed a magnetic measurement system that monitors the local magnetic flux density variations, \(\Delta

|\overrightarrow{B}|\), caused by the change of relative magnetic permeability, μR, with varying temperature inside the processed zone. The new measurement system was applied to a S700MC HSS

to assess the thermal condition inside the through-thickness processed volume. Within the optimal processing temperatures for the HSS, [A1, A3], i.e. around TC, the signal is both

qualitatively and quantitatively sensitive to temperature and to temperature change rates. The concept behind this new system was initially conceived for the control of FSW47. The goal was

to combine the benefits of the solid-state thermomechanical FSW process with a real-time monitoring of the full field processing temperatures. Soon it became clear that this concept is

applicable to a wide range of other relevant steel processing methods (with the appropriate sensor architecture development for each specific application). Thus, this scientific

communication is presented in a generalized approach to thermal and thermomechanical processing applications were it is beneficial that the peak temperatures are inside, or in the vicinity,

of the intercritical temperature region. RESULTS EXPERIMENTAL SETUP We developed a magnetic measurement system tailored to identify temperature evolution in the ideal range for

thermomechanical processing of HSS. Figure 1 shows schematic representations of the measurement setup created to monitor the magnetic flux density during thermal and thermomechanical cycles.

The setup consists of a S700MC HSS test specimen clamped to a non-magnetic copper chassis (Fig. 1a) containing the measurement system. Inside the chassis, a permanent magnet generates a

magnetic field, \(\overrightarrow{H}\), that interacts with the steel specimen, changing the magnetic flux density, \(\overrightarrow{B}\), according to the relation

\(\overrightarrow{B}={\mu }_{R}\cdot \overrightarrow{H}\), assuming that magnetic permeability, _μ__R_, is a scalar since the material is considered isotropic. Two (for redundancy)

Hall-effect sensors, positioned between the magnet and the steel, monitor the local magnetic flux density. The location of these sensors was chosen based on the results of the computational

analysis presented in the ‘Computational analysis’ section. Thermocouples positioned at the half-thickness of the processed zones, according to Fig. 1b, measured the temperatures. The

chassis was water cooled to protect the magnet and the magnetic sensors from the effects of the high temperatures. An oxy-fuel flame was used as the heat source for the thermal cycles (Fig. 

1c), and plastic deformation induced by a rigid friction stir welding (FSW)48,49 tool was the heat source for the thermomechanical cycles (Fig. 1d). These two heat sources were selected to

decouple the purely thermal effect from any eventual effect of the material flow during the thermomechanical processing that might affect the magnetic measurements. Non-electrical heat

sources were selected to avoid any coercive electromagnetic interaction with the magnetic measurement system. A more detailed description of the experimental setup and procedure is described

in the ‘Methods’ section and in the Supplementary Information file accompanying the online version of this publication. PHASE TRANSFORMATION AND CURIE TEMPERATURES OF S700MC STEEL DSC

measurements with different heating and cooling rates (detailed in the ‘Methods’ section) revealed the presence of three distinct peaks in each cycle. These are labelled 1, 2 and 3 in Fig. 

2a. The endothermic peaks inside 1 identify the body centered cubic α iron (e.g. ferrite) → face centred cubic γ iron (austenite) phase transformation between austenite onset temperature,

AC1, and austenite finish temperature, AC3, in the heating stage. The exothermic peaks inside 2 mark the γ → α transformation region between the ferrite onset temperature, AR3, and ferrite

finish temperature, AR1, in the cooling stage. The peaks inside 3 identify TC and their magnitude is smaller than the phase transformation peaks. As with other steels27, the phase change

temperatures depend on the heating/cooling rate but TC is quite stable. A closer analysis of the endothermal reactions during heating at 50 °C/min is presented in Fig. 2b. The peak between

700 and 800 °C corresponds to the ferromagnetic to paramagnetic transformation and its lowest point defines TC = 740 °C. The peak between 800 and 900 °C marks the α ↔ γ phase transformation.

We extrapolated the AC1 and AC3 temperatures by tracing the baseline of the peak and intersecting it with the tangents to the inflection points of the curves. The temperature where the

negative slope tangent intersects the baseline defines AC1 = 826 °C and the temperature where the positive slope tangent intersects the baseline defines AC3 = 882 °C. The austenite to

ferrite transformation onset and finish temperatures on cooling, AR3 and AR1, were determined following the same methodology (Fig. 2c). Since for the 50 °C/min cooling, the TC is inside the

[AR1, AR3] temperature range, the magnetic transformation occurs within the phase transformation and the energetic contributions from these two phenomena are added forming a single

exothermic peak. Considering the relation of the TC with the equilibrium transformation temperatures [A1, A3], an acceptable approximation is [A1, A3] ≈ [AR1, AC3]. COMPUTATIONAL ANALYSIS To

estimate the temperature distribution for the experimental part of this work and to support the design of the magnetic measurement system, we performed computational thermal analyses using

the Finite Element Method (FEM). The analysis established the full temperature fields and identified the volume of material that reaches temperatures above TC, thus, changing from μR≫ 1 to

μR ≈ 1 and becoming paramagnetic, hereafter the paramagnetic volume, Vparamagnetic (Fig. 3). The conditions for the steady-state thermal analysis are described in the ‘Methods’ section.

Superimposing the modelled Vparamagnetic on the etched cross section images of the test specimens reinforces the good agreement between the Vparamagnetic obtained by computational analysis

and the thermomechanically-affected zones (TMAZ) obtained experimentally, further confirming the validity of the model. In a multi-physical approach, we then integrated Vparamagnetic into a

magnetostatic computational analysis to study the interaction of the magnetic field with the test plate upon the ferromagnetic to paramagnetic transformation. The results provide a

visualization of the difference between the magnetic flux density in the presence of a Vparamagnetic in the fully ferromagnetic condition: μR ≫ 1 when T < TC (Fig. 4a,c); _versus_

Vparamagnetic in the paramagnetic condition: μR ≈ 1 when T > TC (Fig. 4b,d). These results were used to support the design of the magnetic measurement system. The optimal position for the

sensors is where the magnetic flux density experiences the greatest variation, comparing the ferromagnetic to paramagnetic states. This occurs mainly inside the paramagnetic volume itself

and in its immediate vicinity. Since the inside of the material is inaccessible and the heat sources occupy the space above the Vparamagnetic, the magnetic sensors were positioned below

Vparamagnetic. EXPERIMENTAL MEASUREMENTS OF TEMPERATURE AND MAGNETIC PERMEABILITY DURING THERMAL AND THERMOMECHANICAL CYCLES The magnetic measurement system, introduced in the ‘Experimental

setup’ section, was used to monitor the magnetic flux density and the temperature during the thermal and thermomechanical cycles (see details in ‘Methods’ section). The different cycles are

identified according to heat source - Flame or FSW tool - and maximum temperature above _or_ below the Curie temperature: TMAX > TC _or_ TMAX < TC. In Figs. 5 and 6, the plotted

temperature curves correspond to the thermocouple that registered the highest temperature in each measurement (i.e. the one closest to the heat source). The magnetic measurements are

represented as magnetic flux density variation, \(\Delta |\overrightarrow{B}|\), from a baseline defined as the initial value of \(|\overrightarrow{B}|\). Positive values of \(\Delta

|\overrightarrow{B}|\) indicate increases of μR in the processed material whereas the opposite applies for negative values of \(\Delta |\overrightarrow{B}|\). The results for the Flame_TMAX 

< TC cycle are presented in Fig. 5a. The maximum temperature does not go over TC and there is no drop in magnetic flux density, indicating that TC was not reached anywhere in the

specimen. Similarly, in the FSW_TMAX < TC cycle (Fig. 5b) the maximum temperature measured did not exceed TC and no drop in Δ\(|\overrightarrow{B}|\) occurs. It is worth mentioning that

even though the whole processed volume of the steel specimens is kept below the Curie temperature the Δ\(|\overrightarrow{B}|\) moves slightly away from the baseline. This phenomena of

sensitivity of the magnetic measurement to different temperatures below the TC is reported by other authors50,51,52. The Flame_TMAX > TC measurements are shown in Fig. 6a. TMAX surpassed

TC and, accordingly, the magnetic flux sensors detected a clear decrease in signal strength, followed by a return to the baseline when the temperature dropped below TC at the end of the

cycle. The magnetic sensors registered the signal decrease about Δt1 = 12.8 seconds before the thermocouple recorded values above TC. This offset is due to the fact that the thermocouple

provides a point measurement while the magnetic measurement is immediately sensitive to the change in μR, caused by temperatures above TC, anywhere in the volume of processed material,

starting from the vicinity of the power source. This delay is opposite during the cooling, for the same reason. Note that Δt2 <  Δt1 which reflects the difference in temperature change

rate between heating and cooling periods. The FSW_TMAX > TC measurements, presented in Fig. 6b, exhibit all the same characteristics as those described for Flame_TMAX > TC, and contain

additional distinguishable features of the notable significance. The distinguishable effect, depicted in Fig. 6b, is an inverse systematic relation between the \(\Delta

|\overrightarrow{B}|\) rate and the heating rate. During the dwell phase of the thermomechanical cycle, the temperature curve exhibits two different heating rates, represented by blue dotted

lines marked \(\frac{\Delta {T}_{1}}{\Delta {t}_{1}}=3.4\) and \(\frac{\Delta {T}_{2}}{\Delta {t}_{2}}=0.2\) °C/s. The two heating rates are reflected in the \(\Delta |\overrightarrow{B}|\)

_versus_ time graph as indicated by blue dotted lines marked \(\frac{\Delta {|\overrightarrow{B}|}_{1}}{\Delta {t}_{1}}=-\,1.1\) and \(\frac{\Delta {|\overrightarrow{B}|}_{2}}{\Delta

{t}_{2}}=-\,0.7\) Gauss/s. This means that the measurement system not only accurately detects the TC, but is also sensitive to the effect of temperature change rates within the processed

volume. This quantitative effect is of the upmost importance because it has not been found in the existing literature and it opens up the possibility of implementing new intelligent control

systems. As an example, the Δ\(|\overrightarrow{B}|\) signal can be used as an input for a control system to maintain the temperatures during steel production or processing inside the

[≈A1,TC] range. The results of a more detailed investigation of the sensitivity of the \(\Delta |\overrightarrow{B}|\) to the volume above Curie temperature, Vparamagnetic, will be presented

next. MAGNETIC FLUX DENSITY MEASUREMENTS VERSUS MATERIAL VOLUME ABOVE CURIE TEMPERATURE We estimated Vparamagnetic, i.e. the volume of material with T > TC, at five different instants

during the heating phase of Flame_TMAX > TC and FSW_TMAX > TC via computational analysis. Figure 7 shows the relationship between Vparamagnetic and the change in magnetic flux density

\(\varDelta |\overrightarrow{B}|\) relative to the initial value \({|\overrightarrow{B}|}_{{t}_{0}}\). Visual representations of the different volumes are included to support the

interpretation of results. Power law curves, _f_(_x_) = _kx__n_, where \(x={V}_{paramagnetic}\) and \(f(x)=\frac{\Delta |\overrightarrow{B}|}{{|\overrightarrow{B}|}_{{t}_{0}}}\), were fitted

to the thermal cycle data (\(k=0.03993\); \(n=0.282\)) and to the thermomechanical cycle data (\(k=0.003636\); \(n=0.574\)). The two curves show that though ΔVparamagnetic is smaller in the

thermal cycle (Flame) than in the thermomechanical cycle (FSW tool) it has a stronger effect on \(\frac{\varDelta |\overrightarrow{B}|}{{|\overrightarrow{B}|}_{{t}_{0}}}\). Observing the

visual representations of the paramagnetic volumes we can identify two different stages in the evolution of \({V}_{paramagneti{c}_{}}\). The first stage is dominated by an increase in the

thickness of \({V}_{paramagneti{c}_{}}\) (i.e. \(\varDelta V\propto \varDelta t\), where t is the thickness) and is more pronounced in \({{\rm{V}}}_{paramagneti{c}_{(Flame)}}\). The second

stage is dominated by radial expansion (i.e. \(\varDelta V\propto \varDelta d\), where _d_ is the diameter) and is more evident in the evolution of

\({{\rm{V}}}_{paramagneti{c}_{(FSWtool)}}\). These results suggest that \(\frac{\varDelta |\overrightarrow{B}|}{{|\overrightarrow{B}|}_{{t}_{0}}}\) is sensitive to the shape of the

paramagnetic volumes and to the way those shapes evolve over time. DISCUSSION The peak temperatures and the temperature change rates control the grain size evolution, precipitation and

solution, which along with the strain hardening are responsible for the microstructure of steels and their mechanical properties. These phenomena depend mostly on the thermal and

thermomechanical history across the intercritical temperature domain12, where the Curie temperature lies and the α ↔ γ phase transformation of iron structures occurs. We developed a

non-destructive, contactless, magnetic-based measurement system that exploits the temperature dependence of the electromagnetic properties to assess temperature domains inside a volume of

processed steel. By monitoring the change of magnetic flux density near the Curie temperature, our system provides real-time qualitative and quantitative information related to the

temperature field within the intercritical temperature domain. This enables the development of intelligent systems capable of assessing and controlling the phenomena that govern the

metallurgical and mechanical properties of steels, which is of special relevance in the thermal and thermomechanical processing of modern high-strength steels. Examples of processes

associated with an external heat source resulting in thermal processing, approximated in the paper by the thermal cycles using the flame as external the heat source, are i) with fusion:

oxi-fuel welding and cutting, laser welding and cutting, electron beam welding, electric arc based welding and cutting; ii) without fusion: heat treatment, e.g. plasma, flame, high-frequency

induction (where the sensor can be integrated with the induction coil). Examples of processes associated with thermomechanical processing, where the heat source is internal, i.e. the

material, by energy dissipation during its bulk plastic deformation, are the FSW (partially addressed in the paper by the thermomechanical cycles using the plunge and dwell stages of a FSW

tool), the friction welding, forging, hot rolling during steel production. The multiphysical research plan encompassed DSC experimental measurements, computational thermal analysis and

dedicated design and implementation of the magnetic-based measurement system. The DSC measurements with different heating and cooling rates were used to establish, with precision and

reliability, the Curie temperature, TC ≈ 740 °C, and the transformation temperatures, [AR1, AC3] = [702 °C, 882 °C], of the S700MC high-strength steel used as test specimen. The

transformation temperatures considered were the ones obtained with the 50 °C/min rate as they are the ones closer to real processing conditions. The Curie temperature showed no dependence on

the heating or cooling rates. The computational thermal analysis was used to support the design of the magnetic measurement system and identify the volume of material that reaches

temperatures above TC, thus, changing from μR ≫ 1 to μR ≈ 1 and becoming paramagnetic. The results show that our magnetic flux density measurements can be used to detect the magnetic

transformation of the processed volume when it reaches the Curie temperature. Above this temperature, it is also sensitive to the effect of temperature change rates within the processed

volume. Additionally, based on the multiphysical approach, the measurements provide sensitive data related to the evolution of the processed volume, namely, it can discern between different

heating and cooling rates and between the effects of different changes in shape (Δ thickness vs Δ diameter). There is a \(\varDelta |\overrightarrow{B}|\) associated with a small magnetic

permeability increase below the Curie temperature indicating that the temperatures inside processed volume are changing, this may also represent a valuable information for a control system

and should be studied in more detail. The new and distinguishable results presented in this work result from two major differences in the implemented research plan when compared with the

state of the art in this field, namely: (i) the measurements of the magnetic properties are performed during transient thermal processing with complex non-homogenous conditions; (ii) besides

an external purely heat power source (i.e. a flame), the work included thermomechanical processing. In this case, the specimen materials become the heat power source, due to the heat

generated by internal viscous energy dissipation during the non-homogeneous plastic deformation of the material and superficial frictional energy dissipation in the contact with the rigid

FSW tool. The internal energy dissipation decreases as the temperature increases and, so, the thermomechanical processing resulted in steady-state heating rates, different for different

stages of the deformation. This yielded the opportunity for the magnetic measurement system to show unique capabilities, besides accurately detecting the TC, such as being sensitive to the

effect of temperature change rates within the processed volume. For full temperature range measurements other complementary measurement methods, such as pyrometers and infrared thermography

systems, can be integrated via data fusion processes. This through-thickness, contactless, monitoring solution (that can provide real-time data on the temperatures and temperature rates

inside a volume of material under non-uniform and transient conditions) will contribute to bring steel production and processing in line with the new digitalization paradigm by providing

large amounts of information rich data that can be readily available to support highly integrated, smart, cyber-physical manufacturing systems53. Going digital in the fabrication of

steel-based structural systems and products, will allow zero-defect factories with safer working conditions and lower environmental impact. The next steps will be to expand the capabilities

of the measurement system from a single Hall-effect sensor configuration to multiple sensors forming an array. This will provide data with spatial resolution and enable image reconstruction

of the processed volume of material. With a dedicated multiphysical solution, integrating computational simulation of the metallurgical evolution and thermal analysis with the

non-destructive real-time magnetic measurement system presented here, it will be possible to deliver a full field imaging solution for application in intelligent automated control systems

for steel production and processing. METHODS MATERIAL The base material used in this study was a S700MC high-strength steel produced by TMCP, whose chemical composition is: [max. wt.%] 0.059

 C; 0.205 SI; 1.79 Mn; 0.007 P; 0.002 S; 0.026 Al; 0.083 Nb; V; 0.013; 0.113 T. The specimens used in the thermal and thermomechanical processing cycles were 100 × 100 × 4 mm plates. For the

thermal cycles (oxy-fuel flame heat source), a region of reduced thickness (2 mm) was produced on the middle of the plates, by removing Ø 25 × 2 mm of material by machining as depicted in

Fig. 1c, to concentrate the heating effect. Similarly, for the thermomechanical cycles (FSW tool heat source) a Ø 10 mm and 3.5 mm deep hole (Fig. 1d) was drilled at the center of the plates

to remove a volume of material roughly equivalent to that of the tool probe. DIFFERENTIAL SCANNING CALORIMETRY (DSC) Differential scanning calorimetry measurements were performed on a

NETZSCH STA 449F1 equipment, capable of a maximum heating rate of 50 °C/s. A sample of the S700MC steel (approximately 1.5 × 2 × 3 mm and 75 mg) was placed inside an Al2O3 ladle and the

measurements were carried out under a protective Argon atmosphere. The thermal cycles comprised four stages: 1 - holding at 100 °C; 2 – heating (at 50, 20, 10, and 5 °C/min); 3 - holding at

1000 °C; and 4 – cooling (at 50, 20, 10, and 5 °C/min). The cycles were carried out three times per heating/cooling rate. The holding times were 5 min. COMPUTATIONAL ANALYSES Transient

thermal computational analyses were performed using the commercial ANSYS Workbench 19.0 software. The purpose of these analyses was to obtain the temperature fields in agreement with the

temperature measurements obtained experimentally via thermocouples and to estimate the volume of material that reached temperatures above TC. The geometries used were the same as shown in

Fig. 1a and 1c, with the specific sample geometry for each heat source (i.e. a region of reduced thickness in the case of the flame as heat source, and the negative of the FSW tool in the

case of the FSW tool as the heat source). The meshes were comprised of about 3.8 million (flame as heat source case) and 3 million (FSW tool as heat source case) tetrahedron elements. The

maximum element size was 0.5 mm in the steel plates and 1 mm in all other bodies. The loading condition representing the flame was a heat flow with a normal distribution applied on the

surface of the reduced thickness region of the steel specimen body. The analysis was carried out in one step. The loading conditions representing the effect of the heat flow from the FSW

tool were applied on the surfaces corresponding to the negative of the tool geometry. The analysis was carried out in two steps. The first step with heat flow applied only on the surfaces

corresponding to the probe, and the second step adding the heat flow contribution on the surfaces corresponding to the shoulder. The final results were obtained by adjusting loading

conditions iteratively until the simulated temperature fields were in close agreement with the thermocouple measurements for each case. In both cases, the initial temperature was 25 °C, and

a constant temperature of 25 °C was applied to the surfaces corresponding to the inside of the copper cooling tubes. An emissivity of 0.3 was considered at the top surface of the steel

specimen, excluding the heat flow loading surfaces. All other outside surfaces were adiabatic. The material models used were those for Steel 1010, Copper, Titanium, and Air, available in the

materials library of the ANSYS Workbench 19.0 software. The results were validated by comparing the temperature fields above the TC, obtained computationally, with the heat-affected zones

evaluated in cross-sections of samples extracted from the center of the processed specimens. A table with the material thermal properties, figures and graphs supporting the methods

implemented in the thermal analyses are included in the “Suplementary Information” file available with the online version of this paper. The magnetostatic computational analyses were

performed using the ANSYS Maxwell R18.0 software. The geometries were the same as in the thermal analyses. The meshes were comprised of 2.8 million tetrahedron elements (in both the flame

and the FSW tool analyses). The volumes obtained from the thermal analysis were integrated into the magnetostatic model and the analyses were carried out for different values of magnetic

permeability (μR ≫ 1 vs μR ≈ 1) in those volumes. The material models used were those for Steel 1010, Copper, Titanium, Air and NdFe35, available in the materials library of the ANSYS

Maxwell R18.0 software. A table with the magnetic properties considered for the materials is included in the “Suplementary Information” file available with the online version of this paper.

THERMAL AND THERMOMECHANICAL CYCLES WITH TEMPERATURE AND MAGNETIC FLUX DENSITY MEASUREMENTS Thermal and thermomechanical cycles were carried out on S700MC HSS using non-electrical heat

sources to avoid any coercive electromagnetic interaction with the magnetic measurement system. Two heat sources were applied to the specimens: For the thermal cycles it was an oxy-fuel

flame, which is a purely thermal heat source; and for the thermomechanical cycles it was the thermomechanical processing, which is an indirect heat source via internal friction dissipation

during the plastic deformation induced in the HSS specimen by the plunging and rotation of a rigid FSW tool. The tool material was a non-magnetic polycrystalline cubic boron nitride in a

tungsten rhenium metal matrix. Thermocouples were inserted into small holes reaching the half thickness of the processed zone of the specimens. A spacing of 5 mm was kept between each

thermocouple as shown in Supplementary Figure S2 in the Supplementary Information file. The ‘Experimental setup’ section described the main features of test setup, depicted in Fig. 1. The

magnet used to generate the magnetic field was a Ø 15 × 8 mm NeFeB permanent magnet with N42 magnetization in the axial direction. The distance from the magnet to the test sample was such

that the interaction between the field and the sample generates the largest field intensity variation when the material changes from ferromagnetic to paramagnetic (and vice versa) without

saturating the signal from the Hall-effect sensors. A good compromise between these two conditions was achieved at a distance of 13 mm, directly under the processed zone. The two sensors

used to measure the magnetic flux density were SS496A1 ratiometric Hall-effect sensors. These were positioned in 2 mm deep slots machined on the copper chassis at ±5 mm from the center of

the plate. The positioning of these sensors, relative to the permanent magnet and the test plate, was supported by the results of the magnetostatic computational analysis. The chassis was

water cooled to protect the magnet and the magnetic sensors from the effects of the high temperatures. Furthermore, a 3 mm thick thermal barrier (air gap for the thermal cycles and a Ti

plate for the thermomechanical cycles) was placed between the copper chassis and the steel test piece for additional protection of the magnet and the sensors from the high temperature, and

also to provide additional backing support in the case of thermomechanical cycles. The data from the Hall-effect sensors and the thermocouples was acquired via a NI USB-6008 module and a

NI-9212 module, respectively. A custom-made application was created in LabVIEW to control and synchronize the data acquisition and recording. The data acquisition rate used was 10 Samples/s

(10 Hz) which was sufficient to capture with high resolution all the magnetic flux density gradients in the tested thermal and thermomechanical transient processes. DATA AVAILABILITY

Supplementary information is available in the document accompanying the online version of this publication. REFERENCES * Zhao, J. & Jiang, Z. Thermomechanical processing of advanced high

strength steels. _Prog. Mater. Sci._ 94, 174–242 (2018). Article  CAS  Google Scholar  * Zhao, M. C., Yang, K. & Shan, Y. The effects of thermo-mechanical control process on

microstructures and mechanical properties of a commercial pipeline steel. _Mater. Sci. Eng. A_ 335, 14–20 (2002). Article  Google Scholar  * Xue, X. H., Shan, Y. Y., Zheng, L. & Lou, S.

N. Microstructural characteristic of low carbon microalloyed steels produced by thermo-mechanical controlled process. _Mater. Sci. Eng. A_ 438–440, 285–287 (2006). Article  CAS  Google

Scholar  * Endo, S. & Nakata, N. Development of Thermo-Mechanical Control Process (TMCP) and high performance steel in JFE Steel. _JFE Tech. Rep._ 20, 1–7 (2015). Google Scholar  *

Movahed, P., Kolahgar, S., Marashi, S. P. H., Pouranvari, M. & Parvin, N. The effect of intercritical heat treatment temperature on the tensile properties and work hardening behavior of

ferrite-martensite dual phase steel sheets. _Mater. Sci. Eng. A_ 518, 1–6 (2009). Article  CAS  Google Scholar  * Shi, L. _et al_. Improved toughness and ductility in ferrite/acicular

ferrite dual-phase steel through intercritical heat treatment. _Mater. Sci. Eng. A_ 590, 7–15 (2014). Article  CAS  Google Scholar  * Shukla, R., Ghosh, S. K., Chakrabarti, D. &

Chatterjee, S. Microstructure, texture, property relationship in thermo-mechanically processed ultra-low carbon microalloyed steel for pipeline application. _Mater. Sci. Eng. A_ 587, 201–208

(2013). Article  CAS  Google Scholar  * Cao, W. _et al_. Ultrahigh Charpy impact toughness (<450J) achieved in high strength ferrite/martensite laminated steels. _Sci. Rep._ 7, 1–8

(2017). Article  CAS  Google Scholar  * Humphreys, F. J., Prangnell, P. B. & Priestner, R. Fine-grained alloys by thermomechanical processing. _Curr. Opin. Solid State Mater. Sci._ 5,

15–21 (2001). Article  ADS  CAS  Google Scholar  * Arora, H. S. _et al_. High Tensile Ductility and Strength in Dual-phase Bimodal Steel through Stationary Friction Stir Processing. _Sci.

Rep._ 9, 1–6 (2019). Article  ADS  CAS  Google Scholar  * Kim, B. C., Lee, S., Kim, N. J. & Lee, D. Y. Microstructure and local brittle zone phenomena in high-strength low-alloy steel

welds. _Metall. Trans. A_ 22, 139–149 (1991). Article  Google Scholar  * Górka, J. Assessment of Steel Subjected to the Thermomechanical Control Process with Respect to Weldability. _Metals

(Basel)._ 8, (169 (2018). Google Scholar  * Górka, J., Janicki, D., Fidali, M. & Jamrozik, W. Thermographic Assessment of the HAZ Properties and Structure of Thermomechanically Treated

Steel. _Int. J. Thermophys._ 38, 1–21 (2017). Article  CAS  Google Scholar  * Thomas, W. M., Threadgill, P. L. & Nicholas, E. D. Feasibility of friction stir welding steel. _Sci.

Technol. Weld. Join._ 4, 365–372 (1999). Article  CAS  Google Scholar  * Lienert, T. & Jr, W. S. Friction stir welding studies on mild steel. _Weld. J. Res. Suppl._ 82, 1–9 (2003).

Google Scholar  * Morisada, Y. _et al_. Improvement of toughness and strength of thick structural steel weld by friction stir welding conditions. _Sci. Technol. Weld. Join._ 18, 287–292

(2013). Article  CAS  Google Scholar  * Xue, P., Komizo, Y., Ueji, R. & Fujii, H. Enhanced mechanical properties in friction stir welded low alloy steel joints via structure refining.

_Mater. Sci. Eng. A_ 606, 322–329 (2014). Article  CAS  Google Scholar  * Fujii, H. _et al_. Friction stir welding of carbon steels. _Mater. Sci. Eng. A_ 429, 50–57 (2006). Article  CAS 

Google Scholar  * Sorger, G. _et al_. Microstructure and fatigue properties of friction stir welded high-strength steel plates. _Sci. Technol. Weld. Join._ 1718, 1–7, 

https://doi.org/10.1080/13621718.2017.1399574 (2017). Article  CAS  Google Scholar  * Sorger, G., Sarikka, T. & Vilaça, P. Effect of processing temperatures on the properties of a

high-strength steel welded by FSW. _Weld. World_, https://doi.org/10.1007/s40194-018-0612-8 (2018). Article  CAS  Google Scholar  * Childs, P. R. N., Greenwood, J. R. & Long, C. A.

Review of temperature measurement. _Rev. Sci. Instrum._ 71, 2959–2978 (2000). Article  ADS  CAS  Google Scholar  * Müller, B., Renz, U., Hoppe, S. & Klocke, F. Radiation Thermometry at a

High-Speed Turning Process. _J. Manuf. Sci. Eng._ 126, 488 (2004). Article  Google Scholar  * Davies, M. A., Ueda, T., M’Saoubi, R., Mullany, B. & Cooke, A. L. On The Measurement of

Temperature in Material Removal Processes. _CIRP Ann. - Manuf. Technol._ 56, 581–604 (2007). Article  Google Scholar  * Kop, T. A., Sietsma, J. & Van Der Zwaag, S. Dilatometric analysis

of phase transformations in hypo-eutectoid steels. _J. Mater. Sci._ 36, 519–526 (2001). Article  ADS  CAS  Google Scholar  * García De Andrés, C., Caballero, F. G., Capdevila, C. &

Álvarez, L. F. Application of dilatometric analysis to the study of solid-solid phase transformations in steels. _Mater. Charact._ 48, 101–111 (2002). Article  Google Scholar  * Kargul, T.

Investigations of Temperatures of Phase Transformations of Low-Alloyed Reinforcing Steel within the Heat Treatment Temperature Range. _Arch. Metall. Mater._ 62, 891–897 (2017). Article  CAS

  Google Scholar  * Raju, S., Ganesh, B. J., Banerjee, A. & Mohandas, E. Characterisation of thermal stability and phase transformation energetics in tempered 9Cr-1Mo steel using drop

and differential scanning calorimetry. _Mater. Sci. Eng. A_ 465, 29–37 (2007). Article  CAS  Google Scholar  * Jeya Ganesh, B. _et al_. Differential scanning calorimetry study of diffusional

and martensitic phase transformations in some 9 wt-%Cr low carbon ferritic steels. _Mater. Sci. Technol._ 27, 500–512 (2010). Article  CAS  Google Scholar  * Ghanei, S., Kashefi, M. &

Mazinani, M. Eddy current nondestructive evaluation of dual phase steel. _Mater. Des._ 50, 491–496 (2013). Article  CAS  Google Scholar  * Zhou, L. _et al_. Quantification of the phase

fraction in steel using an electromagnetic sensor. _NDT E Int._ 67, 31–35 (2014). Article  CAS  Google Scholar  * Yin, W., Peyton, A. J., Strangwood, M. & Davis, C. L. Exploring the

relationship between ferrite fraction and morphology and the electromagnetic properties of steel. _J. Mater. Sci._ 42, 6854–6861 (2007). Article  ADS  CAS  Google Scholar  * Sorger, G. L.

_et al_. Non-destructive microstructural analysis by electrical conductivity: comparison with hardness measurements in different materials. _J. Mater. Sci. Technol_,

https://doi.org/10.1016/j.jmst.2018.09.047 (2018). Article  Google Scholar  * Xu, H. _et al_. Imaging x70 weld cross-section using electromagnetic testing. _NDT E Int._ 98, 155–160 (2018).

Article  CAS  Google Scholar  * Yu, C. _et al_. Measurement of the Hardness of Medium Carbon Steel Using the Magnetic Mixing-Frequency Technique. _IEEE Trans. Magn_. 54 (2018). Article 

Google Scholar  * Makar, J. & Tanner, B. The _in situ_ measurement of the effect of plastic deformation on the magnetic properties of steel. _J. Magn. Magn. Mater._ 184, 193–208 (2002).

Article  ADS  Google Scholar  * Perevertov, O. Influence of the applied elastic tensile and compressive stress on the hysteresis curves of Fe-3%Si non-oriented steel. _J. Magn. Magn. Mater._

428, 223–228 (2017). Article  ADS  CAS  Google Scholar  * Qiu, F., Ren, W., Tian, G. Y. & Gao, B. Characterization of applied tensile stress using domain wall dynamic behavior of

grain-oriented electrical steel. _J. Magn. Magn. Mater._ 432, 250–259 (2017). Article  ADS  CAS  Google Scholar  * Aghadavoudi-Jolfaei, M., Shen, J., Smith, A., Zhou, L. & Davis, C. L.

Non-destructive measurement of microstructure and tensile strength in varying thickness commercial DP steel strip using an EM sensor. _J. Magn. Magn. Mater._ 473, 477–483 (2019). Article 

ADS  CAS  Google Scholar  * Perevertov, O., Stupakov, O., Tomáš, I. & Skrbek, B. Detection of spring steel surface decarburization by magnetic hysteresis measurements. _NDT E Int._ 44,

490–494 (2011). Article  CAS  Google Scholar  * Zhu, W. _et al_. Evaluation of rail decarburisation depth using a H-shaped electromagnetic sensor. _NDT E Int._ 46, 63–69 (2012). Article  CAS

  Google Scholar  * Liu, J. _et al_. Electromagnetic evaluation of the microstructure of Grade 91 tubes/pipes. _Int_. _J. Press. Vessel. Pip._ 132–133, 65–71 (2015). Article  CAS  Google

Scholar  * Cedillo, E., Ocampo, J., Rivera, V. & Valenzuela, R. An apparatus for the measurement of initial magnetic permeability as a function of temperature. _J. Phys. E._ 13, 383–386

(1980). Article  ADS  CAS  Google Scholar  * Morishita, M., Takahashi, N., Miyagi, D. & Nakano, M. Examination of magnetic properties of several magnetic materials at high temperature.

_Prz. Elektrotechniczny (Electrical Rev._ 87,, 106–110 (2011). Google Scholar  * Yamamura, H., Toh, T., Harada, H., Takeuchi, E. & Ishii, T. Optimum magnetic flux density in quality

control of casts with level DC magnetic field in continuous casting mold. _ISIJ Int._ 41, 1229–1235 (2001). Article  CAS  Google Scholar  * Kuz’ko, E. I., Belomyttsev, M. Y. & Belov, V.

A. A Study of Phase Transformations in High-Chromium Ferritic-Martensitic Steels by Magnetometry. _Met. Sci. Heat Treat._ 60, 259–265 (2018). Article  ADS  CAS  Google Scholar  * Harada, H.,

Nagashima, M., Konno, T., Yamana, M. & Toh, T. Electromagnetic sensor just below CC mold by using magnetic transformation of steel. _IOP Conf. Ser. Mater. Sci. Eng_. 424 (2018). *

Sorger, G., Vilaça, P. & Santos, T. G. Concept and Architecture of a New Advanced Control for the FSW of Steels. _Proc. 11th Int. Symp. Frict. Stir Weld_. (2016). * Vilaça, P. &

Thomas, W. In _Structural Connections for Lightweight Metallic Structures_ (eds. Moreira, P. M. G. P., da Silva, L. F. M. & de Castro, P. M. S. T.) 85–124,

https://doi.org/10.1007/8611_2011_56 (Springer Berlin Heidelberg, 2012). Chapter  Google Scholar  * Mishra, R. S. & Ma, Z. Y. Friction stir welding and processing. _Mater. Sci. Eng. R

Reports_ 50, 1–78 (2005). Article  CAS  Google Scholar  * Zhou, L., Hall, R. & Davis, C. L. Measured and modelled low field relative permeability for dual phase steels at high

temperature. _J. Magn. Magn. Mater._ 475, 38–43 (2019). Article  ADS  CAS  Google Scholar  * Boehm, A. & Hahn, I. Measurement of magnetic properties of steel at high temperatures. _Ind.

Electron. Soc. IECON 2014-40th Annu. Conf. IEEE_ 715–721 (2014). * Takahashi, N., Morishita, M., Miyagi, D. & Nakano, M. Examination of magnetic properties of magnetic materials at high

temperature using a ring specimen. _IEEE Trans. Magn._ 47, 4352–4355 (2011). Article  ADS  CAS  Google Scholar  * Monostori, L. _et al_. Cyber-physical systems in manufacturing. _CIRP Ann._

65, 621–641 (2016). Article  Google Scholar  Download references ACKNOWLEDGEMENTS Gonçalo Sorger thankfully acknowledges the financial support provided by the School of Engineering of Aalto

University. Telmo G. Santos acknowledges FCTMCTES for its financial support via the project UID/EMS/00667/2019 (UNIDEMI). AUTHOR INFORMATION AUTHORS AND AFFILIATIONS * Department of

Mechanical Engineering, School of Engineering, Aalto University, 02150, Espoo, Finland Gonçalo Sorger & Pedro Vilaça * UNIDEMI, Department of Mechanical and Industrial Engineering, NOVA

School of Science and Technology, Universidade NOVA de Lisboa, 2829-516, Caparica, Portugal Telmo G. Santos Authors * Gonçalo Sorger View author publications You can also search for this

author inPubMed Google Scholar * Pedro Vilaça View author publications You can also search for this author inPubMed Google Scholar * Telmo G. Santos View author publications You can also

search for this author inPubMed Google Scholar CONTRIBUTIONS G.S., T.G.S. and P.V. contributed to the discussion on the concept, design and applications of the magnetic-based measurement

system. G.S. constructed the measurement system, developed the LabVIEW data acquisition software and carried out all of the experiments. G.S. and P.V. contributed to the computational

thermal analysis. G.S. and T.G.S. contributed to the magnetostatic computational analysis. G.S. and P.V. contributed to the analysis and discussion of results. G.S. and P.V. contributed to

writing the paper. All authors reviewed the manuscript. CORRESPONDING AUTHOR Correspondence to Gonçalo Sorger. ETHICS DECLARATIONS COMPETING INTERESTS The authors declare no competing

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THIS ARTICLE CITE THIS ARTICLE Sorger, G., Vilaça, P. & Santos, T.G. Local magnetic flux density measurements for temperature control of transient and non-homogeneous processing of

steels. _Sci Rep_ 9, 17900 (2019). https://doi.org/10.1038/s41598-019-54503-5 Download citation * Received: 28 June 2019 * Accepted: 14 November 2019 * Published: 29 November 2019 * DOI:

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