Question 2 of 8: Heat-treatment schemes for 1080 steel using the TTT diagram

Question 2: Heat-treatment schemes for 1080 steel using the TTT diagram (20 marks)

Question text not reproduced: the examination questions are © Engineers and Geoscientists BC. Open the official past paper (linked at the top of this page) to read the question, then follow the worked solution below.

Given. AISI 1080 is a plain-carbon steel of eutectoid composition (0.80 wt % C), so its isothermal time–temperature–transformation (TTT) diagram is the classic single-C-curve form: eutectoid temperature A₁ = 727 ℃, nose at roughly 540 ℃ and about 1 s, martensite start M_s ≈ 220 ℃ and martensite finish M_f ≈ −50 ℃.

Find. For each of the five required changes, the austenitising step, the quench path, any isothermal hold, and the final cooling — each traced on the TTT diagram.

One principle governs every part of this question and is worth stating before any individual answer: the TTT diagram describes the decomposition of austenite, and nothing else. Pearlite, bainite and martensite are all products of austenite. None of them transforms directly into another at ordinary temperatures. Consequently, every part of this question except the tempering leg of (b) begins with the same step — re-austenitise — and a candidate who tries to convert pearlite straight into martensite by quenching from room temperature has missed the point of the diagram entirely. A second consequence matters for 1080 in particular: because M_f lies well below room temperature, any treatment demanding 100 % martensite requires a sub-zero (cryogenic) finish, otherwise 5–10 % retained austenite is left behind.

(a) 100 % pearlite → 50 % pearlite + 50 % martensite. Austenitise at about 760 ℃ (some 30 ℃ above A₁) and hold long enough to dissolve all the pearlite into homogeneous austenite — typically 30 min for a section of modest thickness. Quench rapidly to about 620 ℃, which is above the nose, and hold isothermally only until the 50 % transformation curve is reached (read from the diagram, of the order of 15 s at that temperature). At that instant half the austenite has become pearlite. Immediately quench again, fast enough to miss the nose, past M_s and down below M_f: the remaining half of the austenite transforms athermally to martensite. The result is the required 50/50 mixture. The two-stage quench is the whole trick — the hold sets the pearlite fraction, the second quench freezes whatever austenite is left.

(b) 75 % pearlite + 25 % martensite → 100 % tempered martensite. The starting mixture is irrelevant once it is re-austenitised, which is exactly what must be done: heat to about 760 ℃ and hold until both the pearlite and the existing martensite have dissolved into uniform austenite. Now quench severely — brine or agitated water for a plain-carbon steel of this hardenability — so that the cooling curve passes to the left of the nose without touching it, and continue below M_s and then below M_f with a sub-zero treatment to eliminate retained austenite. That gives 100 % (untempered) martensite, which is hard and brittle and in a state of high residual stress. Finally temper: reheat to somewhere between 250 and 650 ℃ depending on the strength–toughness balance wanted, hold about one hour, and air cool. Tempering precipitates the supersaturated carbon as fine cementite in a ferrite matrix. Note that the tempering leg cannot be drawn on the TTT diagram: it starts from martensite, not austenite.

(c) Pearlite → bainite. Austenitise at 760 ℃ as before. Then austemper: quench rapidly into a salt or lead bath held between the nose and M_s — about 350 ℃ is a good choice for lower bainite — fast enough that the cooling curve passes to the left of the nose and no pearlite forms on the way down. Hold isothermally at that temperature until the transformation-finish curve is crossed, which the diagram puts at roughly 10³ s at 350 ℃. Then cool to room temperature in air; the rate no longer matters because there is no austenite left to transform. Austempering has a practical bonus: because the part is held at a uniform temperature while it transforms, distortion and quench cracking are far lower than in a quench-and-temper route to comparable hardness.

(d) Martensite → fine pearlite. Again the route is through austenite. Re-austenitise at 760 ℃, holding long enough for full homogenisation. Then quench to just above the nose — about 580 ℃ — and hold isothermally past the transformation-finish curve, of the order of 30 s at that temperature, before air cooling. The choice of hold temperature is what selects the pearlite spacing: transformation just below A₁ (650–700 ℃) gives coarse pearlite because carbon diffuses far before the lamellae impinge, whereas transformation nearer the nose (540–600 ℃) gives fine pearlite, since the larger undercooling raises the nucleation rate and shortens the diffusion distance. Fine pearlite is both harder and stronger than coarse pearlite of the same composition.

(e) Pearlite → martensite. Austenitise at 760 ℃ and hold to dissolve the pearlite completely. Then quench continuously and severely so that the cooling curve misses the nose — for eutectoid plain-carbon steel that means clearing about 540 ℃ in well under a second, which in practice demands agitated brine and a thin section, since 1080 has poor hardenability and a thick bar will form pearlite at its centre no matter how the surface is cooled. Continue below M_s = 220 ℃; the transformation is athermal, so the martensite fraction depends only on how far below M_s the steel has been taken, not on how long it is held. To reach 100 % martensite the part must be carried below M_f ≈ −50 ℃, so a sub-zero step is required. As-quenched martensite is normally tempered immediately, if only to relieve the quench stresses that otherwise crack the part.