In recent decades, highly alloyed low-density steels are being developed to reduce the weight of different automotive parts. Dilatometry can be a very useful experimental technique to understand phase transformations during heating or cooling of new low-density steel alloys. When performing dilatometry measurements some assumptions are made such as the homogeneity of the sample material tested during the experiment. In this study, dilatometry tests were performed for two different low-density steels, and the variations of the composition between the surface and the inner part of the sample were analyzed. The migration of manganese by diffusion from the interior of the samples and finally its evaporation on the surface under vacuum were observed. This compositional gradient generated in the samples may influence the veracity and interpretation of the results obtained in dilatometry when working with high manganese steel alloys. The detachment of surface grains created by this compositional change near the surface of the samples is also investigated.
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Introduction
The automotive industry has been working on reducing car weight without compromising passenger safety. To this end, they have adopted different strategies such as redesigning components, using high-strength steels and reducing the density of the material used in automobiles. In this last strategy, steel competes strongly with lighter metals, such as aluminum and magnesium. However, steel has the great advantage of being the most recyclable material, which is why low-density steels have been investigated in recent decades. The incorporation of light elements such as aluminum (2.7g/cm3) or silicon (2.33 g/cm3) in steel (7.85 g/cm3), can lead to a reduction in the overall density of the alloy. The addition of 1 wt% of aluminum can result in a total reduction of 1.5% of the steel density (Ref 1). To obtain these low-density steels, it is necessary to start from a steel base composed of iron-carbon, manganese and aluminum (Fe-C-Mn-Al) (Ref 2).
The first information on low-density steels dates back to 1933, when Korter and Ton (Ref 3) first introduced the use of the Fe-Mn-Al-C system. In 1958, Ham and Carin (Ref 4) studied the possibility of replacing Ni and Cr in stainless steels with cheaper metals, such as Mn and Al, due to the advantage of lower density. In the 1980s and 1990s (Ref 5-7) the substitution of Ni and Cr in stainless steel was extensively studied, but until very recently no scientific papers on low density steels have been published in a larger volume.
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The interest generated in this field of application is such that in 2013, the journal Scripta Materialia (Ref 8) published a set of papers (viewpoint papers set) devoted exclusively to low-density steels. The number of patents filed by steel companies on low-density steels (Ref 9-16) in recent years also reflects the interest in these alloys.
For the development of new steel alloys, dilatometry is widely used to study phase transformations (Ref 17-20). Solid-solid phase transformation parameters can be studied due to the difference in specific volumes of the different phases in steel by measuring the change in length of a steel sample during a defined thermal cycle.
However, when using dilatometry, some assumptions are made that do not always hold, as studied in the scientific literature. Regarding the anisotropic deformation of measured samples, Jaramillo and Lusk (Ref 21) distinguished a significant variation in the strain amplitude during thermal processing of a low alloy steel as a function of the orientation of the sample bands. The same authors (Ref 22) and Suh et al. (Ref 23) modeled anisotropic deformation during thermal processing, and highlighted the importance of considering this phenomenon.
Thermal gradients along the sample during dilatometry measurements have also been studied. Mohapatra et al. (Ref 24) revealed that under continuous heating/cooling conditions, when the heating/cooling rate increases, the amplitude of the thermal gradient increases.
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Finally, when the temperature range is above 1000 °C some metal evaporation can occur even in high vacuum dilatometers. This phenomenon, which has been reported for Mn and Cr, causes heterogeneities in the microstructure (Ref 25). The Mn concentration decreases near the surface at high temperature even in vacuum or in a Helium gas atmosphere (Ref 26, 27).
In order to study these phenomena when performing dilatometry experiments with low-density steels, two different low-density alloys, i.e., a duplex and an austenitic steel, were examined using dilatometry measurements at low cooling rates. The microstructures obtained, as well as the deposits created in the dilatometer chamber, have been analyzed. A semi-quantitative measurement of the different elements has been carried out to analyze this phenomenon of evaporation in vacuum. Decohesion of surface grains has also been observed in one of the low-density alloys studied. This phenomenon is discussed in the present manuscript.
Materials and Methods
Two low-density Fe-C-Mn-Al alloy steels were analyzed. Their chemical composition is shown in Table 1.
Table 1
Chemical composition in % of weight, density and relative density reduction compared to the pure iron of the studied low-density steels
Type
C
Mn
Al
Fe
Density, g/cm3
Relative density reduction compared to the pure iron, %
Alloy 1
Duplex
0.35
3.5
5.8
Bal.
7.267
7.71
Alloy 2
Austenitic
1.3
30
10
Bal.
6.737
14.44
In this investigation, a vacuum levitation furnace consisting of a 5-turn induction coil wound around a water-cooled copper crucible, covered by a Pyrex tube and connected to a power supply assisted with vacuum and argon atmosphere was used for sample casting. The crucible is composed of copper segments converging to form a bottom hole from which molten metal can be extracted by removing a refrigerated plug to pour the molten metal into a water-cooled copper mold. These molds can have different geometries depending on the morphological requirements of the final sample. In this study, a cylindrical mold of 30 mm diameter and 100 mm length was used (see Fig. 1a).
Fig. 1
30mm diameter bar obtained from the vacuum levitation furnace (a) and this same bar after being hot forged to 14mm diameter (b)
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The melting procedure was carried out three times to ensure that a homogeneous composition was reached. The bars were hot forged to a diameter of 14mm (see Fig. 1b). Subsequently, normalization was performed prior to dilatometry measurements: 14 mm diameter and 30 mm long bars of Alloys 1 and 2 of were placed in a furnace and heated to 1150 °C with a heating rate of 5 °C/min, then held at that temperature for half an hour and then cooled in air. From the center of these 14 mm diameter bars, samples of 4 mm diameter × 10 mm height were cut by wire electrical discharge machining, then grinded and finally used for dilatometry study (see Fig. 2). After machining, the samples were cleaned by immersion in ethanol inside an ultrasound bath (to remove dirt and oils from the surface of the samples) and, just before the test, they were cleaned again with ethanol.
Fig. 2
4mm diameter sample with the thermocouples attached inside the dilatometer
×
Figure 3 shows the microstructure before dilatometry experiments. Alloy 1 shows a ferrite and martensite microstructure, while Alloy 2 shows an austenitic microstructure.
Fig. 3
Alloy 1 presents a ferritic and martensitic microstructure approximately 50% each (a) and Alloy 2 presents a 100% austenitic microstructure (b)
×
Simulations were performed with JMatPro to determine solidus and liquidus temperature of the alloys in order to define the maximum heating temperature of the dilatometry measurements for the two low-density alloys (see Fig. 4).
Fig. 4
Phases present at different temperatures obtained with JMatPro for Alloy 1 (a) and Alloy 2 (b)
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Dilatometry was performed in a BÄHR DIL805L high-vacuum dilatometer. Based on JMatPro estimates, the specimens were heated to a temperature at least 100 °C below the solidification temperature of each steel. To control the temperature, a thermocouple was welded to the surface (see Fig. 2), which allows the heating and cooling rates to be regulated.
The test conditions were as follows: heating at 3 °C/s up to 1100 °C for Alloy 1 and up to 1050 °C for Alloy 2, holding at that temperature for 5 min and then controlled cooling at 0.01 °C/s. The test time for the samples was approximately 25 h to cool from the heating temperature to 200 °C.
The images in Fig. 3, 6(a), 7(a), 8, 9 and 11 were obtained with a JEOL JSM-7000F scanning electron microscope. The images in Fig. 12 and 14 were obtained with a ZEISS MERLIN scanning electron microscope. x-ray diffraction (XRD) measurements in Fig. 10 were performed with a Bruker D8 Discover 150 diffractometer equipped with a Cr Twist tube.
Results and Discussion
For the dilatometry study, 4mm diameter samples were taken from the inside of the 14mm diameter normalized samples. After the dilatometry tests, the heating and cooling curves of alloy 1 and its derivatives are shown in Fig. 5.
Fig. 5
Dilatometry length curves of the heating (Heating L dash line) and cooling (Cooling L continuous line) of Alloy 1 and its derivatives (Heating D dash line and Cooling D continuous line)
×
The dilatometry curves in Fig. 5 do not show a clear phase change and the slopes are not straight, which is indicative of a continuous transformation between two phases coexisting over a wide temperature range. It appears that on heating a slightly more pronounced change appears around 750ºC, which, according to JMatPro calculations (see Fig. 4a) is associated with the transformation of ferrite to austenite. On cooling, it appears that the most pronounced change occurs around 650-700ºC, perhaps due to the formation of the Kappa phase; again according to JMatPro calculations (see Fig. 4a).
The dilatometry curves for Alloy 2 were not plotted correctly due to the detachment of the thermocouple from the sample surface during the measurement. The reason for the thermocouple detachment will be explained in detail at the end of this section.
When analyzing the samples after dilatometry, the creation of a thick outer layer was observed (see Figs. 6a and 7a). The compositional difference between the surface and the inner part was very large after dilatometry tests. To measure this compositional gradient, semi-quantitative EDX analysis was performed on both samples. The results are presented in Fig. 6(b) and 7(b).
Fig. 6
Image of SEM (a) and semi-quantitative EDX of the compositional gradient of Al and Mn content following the black line from the surface to the inner part for Alloy 1 (b)
Fig. 7
Image of SEM (a) and semi-quantitative EDX of the compositional gradient of Al and Mn content following the black line from the surface to the inner part for Alloy 2 (b)
×
×
A variation in Mn content is observed in both samples. The Mn content is close to zero at the surface and increases continuously until it reaches a maximum at the interface of the inner zone, where it rises sharply to the nominal Mn percentage. This behavior is, especially noticeable in Alloy 2.
The thickness of the gradient layer is 115 microns for Alloy 1 and 70 microns for Alloy 2. This compositional gradient has created a completely different microstructure between the inside and outside of the samples.
Electron Backscatter Diffraction (EBSD) and x-ray diffraction (RXD) measurements were performed on the samples to identify the phases presented in the microstructures of the samples in Fig. 6a and 7a. These results are presented in Fig. 8 and 9. The Kappa phase was not indexed during the EBSD measurements due to the small size of its precipitates.
Fig. 8
EBSD results for Alloy 1 with a step size of 2 micron. Euler angles orientations of the grains (a) and indexed phases (mainly ferrite and some austenite) (b)
Fig. 9
EBSD results for Alloy 2 with a step size of 5 micron. Euler angles orientations of the grains (a) and indexed phases (ferrite in the exterior and austenite inside) (b)
×
×
The graphs of the XRD measurements are shown in Fig. 10. The microstructure of the samples is textured due to deformation during the forging process.
Fig. 10
XRD graphs of the phases present for the Alloy 1 (top) and Alloy 2 (bottom)
×
In the case of Alloy 1, the outer layer is formed by a structure with large ferrite grains, while in the inner part two phases are present. These two phases are ferrite and austenite and can be distinguished in the compositional graph in Fig. 6(b), as well as in the EBSD images in Fig. 8. The ferritic grains are richer in aluminum and have less manganese, while the austenitic grains are richer in manganese and have less aluminum. The measured oscillations in composition match perfectly with the position of the grains of the different phases.
In the case of Alloy 2, the surface layer is composed of large ferrite grains, as both alloys have the same composition on the surface, and the inner part is formed by large austenitic grains (see Figs. 7 and 9) with some precipitates within these big grains and at the grain boundaries.
According to the shape of the precipitates (see Fig. 11), their composition (see Table 2) obtained by EDX analysis and XRD results (see Fig. 10), these precipitates are expected to be the Kappa phase or similar.
Fig. 11
Microstructure of the inner part of Alloy 2. Austenite matrix with Kappa phase precipitates
Table 2
Chemical composition (wt%) of different phases present in the inner part of Alloy 2
Al
Si
Mn
Fe
F1
11.85
0.1
31.8
56.25
F2
11.76
0.09
31.59
56.55
F3
9.57
0.27
29.16
61
F4
9.27
0.23
29.32
61.18
×
During each of the dilatometry measurements, a tantalum plate was introduced into the dilatometer chamber to collect the possible deposits generated during the experiment. Tantalum was chosen because of its different chemical composition compared to the alloys studied. Over the tantalum plate, there was a continuous and abundant deposit with the appearance of viscous or semi-liquid film that forms gravity waves (see Fig. 12). After each test, these deposits were analyzed by EDX. In Table 3 there is a comparison of the percentage of Mn and Al found over the tantalum plate deposits. The percentage of Mn found proves that there is a greater evaporation of this element when compared with Al. In the case of Alloy 1, there is no Al found and for Alloy 2 the Mn percentage found in the deposits is more than 5 times higher the Al, while in the sample this percentage is only 3.
Fig. 12
Deposits collected on the tantalum plate inside the dilatometry chamber after testing Alloy 2 at 1050 °C with a cooling rate of 0.01 °C/s
Table 3
Al and Mn content of the deposits over the tantalum plate of the dilatometry chamber in % of weight after testing Alloy 1 at 1250 °C and Alloy 2 at 1050 °C with a cooling rate of 0.01 °C/s
Al
Mn
Alloy 1 deposit
.
8.76
Alloy 2 deposit
1.8
9.54
×
The deposits in the dilatometer chamber present the same elements in their composition as the alloys measured, although with a higher proportion of manganese. The amount of manganese collected on the tantalum plate is higher for Alloy 2 due to its higher content of this element although the dilatometry was performed at lower temperature.
Due to the topology of these deposits (see Fig. 12), a semi-liquid condensation appears, which could have its origin in the sublimation of the metallic elements on the surface of the dilatometry specimen.
The increase in manganese content in the deposits indicates that manganese evaporates at a higher rate than iron and aluminum.
In both alloys, there is a remarkable alteration of the chemical composition in the surface layer. The layer is enriched in Fe and Al and is depleted in Mn by diffusion and evaporation phenomena ranging from 70 to 115 microns.
These results are in good agreement with those of Catteau et al. (Ref [25]). They performed vacuum dilatometry experiments on a 0.35C-1.2Mn-0.7Cr-0.1Mo-0.1V (in mass %) steel, austenitized at 1150 °C for 3 min, rapidly cooled to 600 °C, held for 25 min, and then gas quenched to room temperature. They also observed the evaporation of Mn to a depth of 10 microns.
This change in the microstructure of the surface layer can cause cracking problems when producing low-density alloys using current industrial processing routes, as reported by S. Chen et al. (Ref 28).
Theoretical calculations were performed to understand the relationship between the Mn diffusion distance and the depth of the depleted zone. Mn profiles were then calculated for both alloys using the second Fick diffusion equation according to (Ref 26).
The data used for these calculations are as follows:
For Alloy 1: Mn content= 3%, Heating temperature= from 293K to 1373K, Heating rate= 3 °C/s (360 sec heating time), Holding time= 300 sec, Cooling rate from 1373 to 473K= 0.01 °C/s (90.000 sec. cooling time), R (J/mol·K) = 8.31, Pre-exponential factor D0 (m2/s) = 9.60E-07, Activation energy for diffusion Q (kJ/mol) = 222 (D0 and Q taken from Table 2 in (Ref 29)).
For Alloy 2: Mn content= 30%, Heating temperature= from 293K to 1323K, Heating rate= 3 °C/s (343 sec heating time), Holding time= 300 sec, Cooling rate from 1323 to 293K= 0.01 °C/s (85.000 sec. cooling time), R (J/mol·K) = 8.31, Pre-exponential factor D0 (m2/s) = 7.30E-06, Activation energy for diffusion Q (kJ/mol) = 242 (D0 and Q taken from Table 2 in (Ref 30)).
Theoretical Mn content for the dilatometry samples of Alloy 1 and Alloy 2 is plotted in Fig. 13.
Fig. 13
Mn content after theoretical calculation for Alloy 1 and Alloy 2
×
The difference between the depleted zones of the two alloys is shown in Fig. 13. The manganese depleted distance for Alloy 1 is twice the zone obtained for Alloy 2. This result aligns with the experimental results presented in this work and indicates a higher diffusivity of manganese for Alloy 1 compared to Alloy 2. The theoretically calculated manganese profiles are smaller in terms of depths of the depleted zones for both alloys when compared to the physical dilatometry experiments. This difference can be attributed to the lack of data in the scientific literature for accurate diffusion coefficients for the alloys studied in this work. In addition, phase transformations in our studied alloys may influence the diffusion of Mn and the obtained depletion depth.
A second phenomenon was occurred during dilatometry measurements on these low-density alloys. Smaller ferrite grains were detached on the surface of the sample (Fig. 14a). This phenomenon occurs in both alloys, but is more pronounced in Alloy 2, with a higher Al content on the surface.
Fig. 14
Surface topography of the dilatometry specimen of Alloy 2 where the hollows of detached polygonal ferrite grains are observed (a, b)
×
A rough, shiny layer appears on the entire surface of the samples (Fig. 14b). Polygonal cells with sharp edges were observed under the microscope (Fig. 14c). According to EDX results, they are formed by Fe-Al with traces of manganese. There is also oxygen in the sample, which is present in the dilatometer chamber, as shown in Table 3.
The effect of migration and evaporation of Mn in the outermost layer makes it practically possible to form an Fe-Al alloy.
According to the Fe-Al phase diagram (see Fig. 15), at high temperature the ferrite is stable (with a minimum Al content of 1.95%) and so is the Fe3Al phase. Above 1022 °C and, especially from 1092 °C the Fe3Al phase can decompose into other aluminum enriched phases. At T < 1215 °C (1171 °C) the Fe3Al phase can segregate liquid Al. Therefore, the outermost surface layer may be in the above conditions at T > 1100 °C and segregate phases that are either liquid, limiting the cohesion of the steel and facilitating the detachment of grains from the outermost surface layer. As mentioned at the beginning of this section when presenting the dilatometry results, the detachment of the surface grains may be the reason for the disconnection of the thermocouple from the surface of Alloy 2 during the performance of the dilatometry measurement. This detachment of the thermocouple made it impossible to obtain the complete dilatometry curve.
Fig. 15
Fe-Al diagram. Republished with permission of ASM International, from “Fe–Al Binary Phase Diagram,” ASM Handbook, Vol. 3, Alloy Phase Diagrams, J.L. Murray, 2nd ed., H. Baker, Ed., 1992; permission conveyed through
Although Alloy 2 was heated up to 1050 °C this temperature may be higher when the pressure decreases (Ref 31). Their study concludes that the transition temperature of delta iron to liquid increases with pressure based on the Clausius-Clapeyron formula. In this study the pressure decreases with vacuum inside the dilatometer chamber, so it is expected that the transition temperature of delta iron from solid to liquid also decreases.
Conclusions
Manganese migration and subsequent evaporation were observed in the two low density alloys examined by vacuum dilatometry measurements. This manganese migration produced a thick layer on the outer section of the samples with a heterogeneous composition gradient that created a different microstructure on the surface. This layer with different composition and properties of the bulk material can grow up to 0.11 mm for dilatometry experiments with a manganese content of 30% and a cooling rate of 0.01 °C/s, affecting up to 10.7% of the total volume of the 4 mm diameter samples. This compositional gradient could affect the conclusions of dilatometry measurements, leading to misinterpretation of the results when working with steel alloys with high manganese content. Sufficient diameter samples and shorter duration tests should be prioritized whenever possible when performing dilatometry with high manganese steel alloys to minimize this problem.
Another phenomenon was observed in the two low density alloys, but especially in alloy 2. Due to the complete evaporation of Mn from the surface of the samples, a Fe and Al rich layer was created on the surface. This Fe-Al alloy can create decomposition of the surface particles at high temperatures. The melting of the newly created Fe-Al phase at high temperature can cause detachment of the surface grains from the large ferritic grains. This phenomenon can cause problems during dilatometry testing, such as detachment of the thermocouples from the surface of the samples.
Acknowledgments
The authors thank for technical and human support provided by SGIker of UPV/EHU and European funding (ERDF and ESF).
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