What is The Eutectoid Reaction in Steel?

The Eutectoid Reaction in Steel is a fundamental microstructural concept in steel metallurgy that determines mechanical properties including strength, toughness, and hardness. It forms during solid-state phase transformations of austenite under specific temperature and time conditions defined by the TTT and CCT diagrams.

How does it affect mechanical properties?

The morphology, distribution, and fraction of microstructural constituents directly control yield strength (via Hall-Petch and precipitation strengthening), impact toughness (via grain size and phase distribution), and hardness (via carbon content in each phase). Optimising heat treatment to control microstructure is the primary method for achieving target mechanical properties in engineering steels.

How is it identified in metallographic sections?

Optical metallography with nital (2% HNO3 in ethanol) or picral (4% picric acid in ethanol) etching reveals most steel microstructural constituents at 100-500× magnification. Scanning electron microscopy (SEM) provides higher resolution identification, while EBSD (electron backscatter diffraction) gives crystallographic phase identification. Reference: ASM Handbook Vol. 9: Metallography and Microstructures.

Eutectoid Reaction in Steel: γ → α + Fe₃C

This article provides a comprehensive technical guide to The Eutectoid Reaction in Steel — Austenite to Pearlite at 0.77%C, 727°C —
a fundamental concept in physical metallurgy that underpins the understanding of steel
microstructure, heat treatment, deformation behaviour, and mechanical properties.
This is essential knowledge for metallurgists, materials engineers, welding engineers,
and advanced engineering students.

KEY TAKEAWAYS

Figure: Iron-Carbon (Fe-Fe₃C) Phase Diagram showing all phases, A1 eutectoid line (727°C, orange dashed), A3 boundary (green), eutectoid point S (0.77%C), and eutectic point C (4.3%). © metallurgyzone.com/

The Eutectoid Reaction in Steel is a fundamental microstructural concept in steel and metals.
Formation depends on chemical composition, temperature, cooling rate, and prior processing history.
Microstructure directly determines mechanical properties: strength, toughness, hardness, and ductility.
Identification requires optical metallography with appropriate etching or electron microscopy techniques.
All steel heat treatment is designed to control the formation and distribution of these microstructural constituents.

📷 IMAGE: eutectoid pearlite colony optical high magnification lamellae ferrite cementite

High-magnification optical micrograph (1000×) of pearlite in a eutectoid steel (0.77%C), transformed isothermally at 630°C. Individual colonies are visible as regions of parallel lamellae with a common orientation. The interlamellar spacing S₀ ≈ 180 nm at this transformation temperature. Different colonies show different apparent spacings due to sectioning angle.

Search terms: pearlite colony eutectoid steel optical micrograph 1000x lamellae

Source:

https://en.wikipedia.org/wiki/Pearlite

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Formation Mechanism and Thermodynamics

The formation of this microstructural constituent is governed by the thermodynamics of phase stability and the kinetics of atomic diffusion. The driving force for transformation is the reduction in Gibbs free energy when the parent phase (typically austenite) transforms to the more stable product phase(s) below the equilibrium transformation temperature. The rate of transformation depends on the competition between this thermodynamic driving force and the kinetic barriers — primarily atomic diffusion through the crystal lattice.

Key thermodynamic and kinetic parameters:

Transformation driving force: ΔG = G_product − G_parent < 0 (thermodynamically favourable)
Transformation rate: depends on nucleation rate J and growth rate G
Avrami kinetics: f = 1 − exp(−kt^n)  [isothermal transformation]
Diffusion: D = D₀ × exp(−Q/RT)  [Arrhenius temperature dependence]

Crystallographic Features and Morphology

Many steel microstructural constituents form with specific crystallographic orientation relationships with the parent austenite phase. These relationships minimise the interface energy and transformation strain, maintaining atomic registry at the habit plane interface:

Kurdjumov-Sachs (K-S) relationship:

  {{111}}_γ ∥ {{110}}_α  and  ⟨110⟩_γ ∥ ⟨111⟩_α

  Gives 24 possible orientation variants within one prior austenite grain
Nishiyama-Wassermann (N-W) relationship:

  {{111}}_γ ∥ {{110}}_α  and  ⟨112⟩_γ ∥ ⟨110⟩_α

  Gives 12 orientation variants

Mechanical Properties

Property	Effect of Finer Scale	Effect of Higher Carbon	Effect of Alloying Elements
Yield strength	Increases (Hall-Petch)	Increases (solid solution + precipitation)	Varies by mechanism
Tensile strength	Increases	Increases significantly	Generally increase
Elongation	Usually improves	Reduces at same hardness	Mo, Ni improve toughness
Charpy toughness	Improves (finer grain = shorter crack path)	Reduces (more brittle phases)	Ni improves; V may reduce
Hardness	Increases	Increases significantly	Cr, Mo, V increase

Industrial Significance and Applications

Understanding and controlling the formation of this microstructural constituent is essential for:

Steel selection: Specifying the appropriate grade for the target microstructure achievable with available heat treatment equipment and section size
Heat treatment design: Setting austenitising temperature, soak time, cooling rate, and tempering cycle
Quality control: Metallographic verification that the specified microstructure has been achieved
Welding procedure development: Predicting and controlling HAZ microstructure to meet toughness and hardness requirements
Failure analysis: Identifying unexpected microstructural constituents that contributed to premature failure

📷 IMAGE: cooperative ferrite cementite eutectoid growth mechanism diagram

Schematic of cooperative pearlite growth. Carbon rejected ahead of growing ferrite diffuses laterally to feed adjacent cementite plates, which in turn reject iron atoms back to the ferrite. Both phases grow at the same rate from a common transformation front. The interlamellar spacing S₀ is inversely proportional to undercooling below 727°C: S₀ ∝ 1/ΔT.

Search terms: cooperative growth eutectoid reaction ferrite cementite diffusion schematic

Source:

https://en.wikipedia.org/wiki/Pearlite#Formation_mechanism

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Frequently Asked Questions

Q: How is this constituent identified in optical metallography?

A: Optical identification relies on: (1) polishing to 0.05µm OPS finish; (2) etching with appropriate etchant — nital (2% HNO₃ in ethanol) for most carbon and low-alloy steels reveals most microstructural constituents through preferential attack of grain boundaries and phases; picral (4% picric acid) preferentially reveals cementite; Klemm’s reagent distinguishes bainite from martensite; (3) observation under bright-field reflected light at 100–500× magnification; (4) comparison with reference micrographs in ASM Handbook Vol. 9: Metallography and Microstructures.

Q: How does cooling rate affect which constituent forms?

A: Cooling rate is the primary variable that determines which austenite transformation product forms, via the CCT diagram. Fast cooling (water quench: 100–300°C/s) bypasses all diffusion-controlled transformations and produces martensite below Ms. Intermediate cooling (oil quench: 20–60°C/s or forced air: 3–15°C/s) may pass through the bainite C-curve, producing bainite or mixed bainite+martensite. Slow cooling (air: 0.5–2°C/s or furnace: 0.01–0.1°C/s) passes through the pearlite region, producing pearlite+ferrite for hypoeutectoid steels. The specific temperatures and times depend on the steel composition via the CCT diagram.

Q: What alloying elements are most effective at controlling microstructure formation?

A: For retarding pearlite and bainite (increasing hardenability for martensite formation): Mo is most effective specifically for suppressing pearlite while moderately affecting bainite. Cr and Mn retard both pearlite and bainite. Ni primarily retards pearlite. B (0.001–0.003%) is highly cost-effective for increasing hardenability in low-alloy steels. For grain refinement (improving toughness): Nb, Ti, and Al (as AlN) pin austenite grain boundaries below 1100°C, limiting grain growth during austenitising. For precipitation strengthening of ferrite: V (as VC precipitates at γ/α interface during cooling), Nb (NbC), and Ti (TiC).

References

Bhadeshia, H.K.D.H. and Honeycombe, R., Steels: Microstructure and Properties. 4th ed. Butterworth-Heinemann, 2017.
Krauss, G., Steels: Processing, Structure, and Performance. 2nd ed. ASM International, 2015.
ASM Handbook Vol. 9: Metallography and Microstructures. ASM International, 2004.
Callister, W.D. and Rethwisch, D.G., Materials Science and Engineering. 10th ed. Wiley, 2018.