Carbide Precipitation in Electrical Steels

Michal, G. M.; Slane, J. A.

doi:10.1007/bf03257952

Cited by 5 publications

(4 citation statements)

References 10 publications

Supporting

Mentioning

Contrasting

Order By: Relevance

“…The maximum coercivity occurs for carbide particles of size 1.0-1.5 pm. This result was confirmed independently by the work of Leslie and Stevens (1964) and by Michal and Slane (1985).…”

Section: Magnetic Properties and Microstructure Of Carbon Steelssupporting

confidence: 58%

Magnetic properties and microstructure of AISI 1000 series carbon steels

Jiles

1988

J. Phys. D: Appl. Phys.

100

View full text Add to dashboard Cite

The magnetic properties of a number of specimens of AISI 1000 series plain carbon steels have been measured as functions of chemical composition, microstructure and heat treatment. The results showed that for a given morphology of the carbides the magnetic properties such as coercivity and permeability varied smoothly as a function of carbon content. Coercivity increased with carbon content by 2.0 Oe for every 0.1 wt.% carbon added at low carbon contents while initial permeability decreased by 57% on the addition of 0.2 wt.% carbon in the form of lamellar carbides (pearlite), but by only 21% when those carbides were in the form of spheroidised particles. In all cases the spheroidised specimens were found to be magnetically softer than the lamellar specimens and the difference increased with the amount of carbon present. Grain size did not seem to affect the magnetic properties significantly above a carbon content of 0.2 wt.%, although it was known that grain size is a significant factor in determining magnetic properties in iron alloys with lower carbon content.

show abstract

“…The maximum coercivity occurs for carbide particles of size 1.0-1.5 pm. This result was confirmed independently by the work of Leslie and Stevens (1964) and by Michal and Slane (1985).…”

Section: Magnetic Properties and Microstructure Of Carbon Steelssupporting

confidence: 58%

Magnetic properties and microstructure of AISI 1000 series carbon steels

Jiles

1988

J. Phys. D: Appl. Phys.

100

View full text Add to dashboard Cite

show abstract

“…[64,65] Many others have reported that elevated Si content shifts the temperature range for both austenite decomposition and cementite precipitation to higher temperatures. [9,13,31,42,46,[50][51][52][66][67][68][69][70][71][72][73][74] In contrast, the maxima in CVN impact energy vs tempering temperature that marks the start of TME are at 200°C for both the SAE 4130 steel with low silicon [65] and the MCHSS with 3.2 at. pct Si of this study.…”

Section: Mö Ssbauer Spectral Resultsmentioning

confidence: 99%

Characterization of the Carbon and Retained Austenite Distributions in Martensitic Medium Carbon, High Silicon Steel

Sherman

Cross

Kim

et al. 2007

Metall Mater Trans A

View full text Add to dashboard Cite

The retained austenite content and carbon distribution in martensite were determined as a function of cooling rate and temper temperature in steel that contained 1.31 at. pct C, 3.2 at. pct Si, and 3.2 at. pct noniron metallic elements. Mo¨ssbauer spectroscopy, transmission electron microscopy (TEM), transmission synchrotron X-ray diffraction (XRD), and atom probe tomography were used for the microstructural analyses. The retained austenite content was an inverse, linear function of cooling rate between 25 and 560 K/s. The elevated Si content of 3.2 at. pct did not shift the start of austenite decomposition to higher tempering temperatures relative to SAE 4130 steel. The minimum tempering temperature for complete austenite decomposition was significantly higher (>650°C) than for SAE 4130 steel (~300°C). The tempering temperatures for the precipitation of transition carbides and cementite were significantly higher (>400°C) than for carbon steels (100°C to 200°C and 200°C to 350°C), respectively. Approximately 90 pct of the carbon atoms were trapped in Cottrell atmospheres in the vicinity of the dislocation cores in dislocation tangles in the martensite matrix after cooling at 560 K/s and aging at 22°C. The 3.2 at. pct Si content increased the upper temperature limit for stable carbon clusters to above 215°C. Significant autotempering occurred during cooling at 25 K/s. The proportion of total carbon that segregated to the interlath austenite films decreased from 34 to 8 pct as the cooling rate increased from 25 to 560 K/s. Developing a model for the transfer of carbon from martensite to austenite during quenching should provide a means for calculating the retained austenite. The maximum carbon content in the austenite films was 6 to 7 at. pct, both in specimens cooled at 560 K/s and at 25 K/s. Approximately 6 to 7 at. pct carbon was sufficient to arrest the transformation of austenite to martensite. The chemical potential of carbon is the same in martensite that contains 0.5 to 1.0 at. pct carbon and in austenite that contains 6 to 7 at. pct carbon. There was no segregation of any substitutional elements.

show abstract

“…Specimens A-2 and B-2 were carburized to produce different carbon contents; the chemical compositions of the specimens before and after carburization are shown in Table 1. All specimens were heated to 900 °C in a dry N2 atmosphere and water cooled at a cooling rate of more than 40 °C/s to ensure a solid solution of carbon in accordance with the literature 23,24) . Fig.…”

Section: Experimental Methodsmentioning

confidence: 99%

Influence of Initial Crystal Orientation and Carbon Content on Rolling-induced Texture in 3 Mass% Si Steel

Shingaki¹,

Takashima²,

Hayakawa³

2022

ISIJ Int.

View full text Add to dashboard Cite

The influence of the initial crystal orientation and carbon content on rolling-induced texture was investigated using quasi-single crystals of 3.2 mass% Si steel. These specimens had {110}<001> and {110}<113> crystal orientations, which are common near surface textures for hot-rolled steel band. In the case of ultralow-carbon specimens, the initial {110}<001> orientation rotated to {111}<112> after 66% reduction cold rolling and the initial {110}<113> orientation rotated to near {211}<124>. It is considered that the crystal rotation from {110}<113> to near {211}<124> is caused by activation of the {110} slip system, which has the second largest Schmid factor. The {211}<124> orientation is not considered to be a stable rolling-induced texture; however, the {211}<124> orientation was well developed in the present experiments. In addition, the {211}<124> orientation has a geometric characteristic that if it rotates by activation of one slip system, it will revert to the initial {211}<124> crystal orientation by activation of another slip system. In the case of specimens containing carbon, the {110}<001> orientation rotated to {111}<112> and {100}<011> due to deformation twinning. On the other hand, the {110}<113> orientation rotated from the {211}<113> orientation to the {111}<112> orientation during cold rolling. Deformation twinning was also observed. It is considered that the crystal orientation of the deformation twins rotated to near {111}<112> by activation of the {110} slip system.

show abstract

Carbide Precipitation in Electrical Steels

Cited by 5 publications

References 10 publications

Magnetic properties and microstructure of AISI 1000 series carbon steels

Magnetic properties and microstructure of AISI 1000 series carbon steels

Characterization of the Carbon and Retained Austenite Distributions in Martensitic Medium Carbon, High Silicon Steel

Influence of Initial Crystal Orientation and Carbon Content on Rolling-induced Texture in 3 Mass% Si Steel

Contact Info

Product

Resources

About