Materials for engineering, 3rd Edition - (Malestrom)

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Metals and alloys 107 1700 Strength (MN m –2 ) 1250 800 350 40 0.52% C, 0.93% Mn Tensile strength 0.48% C, 0.57% Mn Yield strength Elongation (%) 30 20 Elongation 10 250 350 450 550 650 Tempering temperature (°C) 3.24 The effect of tempering temperature upon tensile properties of a carbon steel. 80 70 60 Temperature (K) 300 400 500 600 700 800 900 wt% Mo 5.0 Hardness (rockwell C) 50 40 30 20 0.35 wt% carbon 2.0 0.5 10 0 0 100 200 300 400 500 600 700 Temperature (°C) 3.25 Showing secondary hardening during tempering of a Mobearing steel.
108 Materials for engineering The progressive fall in hardness with increasing tempering temperature arises because of the rapidly increasing diffusivity of carbon, allowing progressively coarser particles of iron carbide to form in the steel. Highspeed steels contain major additions of strong carbide-forming elements such as Cr, Mo, W and V. When these steels are quenched and tempered, alloy carbides form in the high-temperature range when the hardness of plain-carbon steels declines, so secondary hardening (Fig. 3.25) is observed. High-speed steels are so called because they maintain their hardness during high-speed machining operations: appreciable softening does not occur until the temperature exceeds about 550°C, which represents the maximum operating temperature for these steels. Pearlitic steels As apparent from Fig. 3.21, air-cooled medium- to high-carbon steels undergo a eutectoid decomposition to form a microstructure of islands of lamellar pearlite (α + Fe 3 C) in an α matrix and their strength will increase as the volume fraction of pearlite increases as illustrated in Fig. 3.26. Their applications include rail steels, as well as high-carbon wire rod. The latter are transformed from γ at a temperature near the ‘nose’ of the TTT curve (Fig. 3.23) to form a microstructure of minimum interlamellar spacing. The wire is then cold drawn, and the work-hardened product may have tensile strengths in excess of 2 GPa. Bainitic steels Steel transformed at temperatures below the ‘nose’ of the TTT curve form a non-lamellar aggregate of α + Fe 3 C known as ‘bainite’, which consists of fine plates of ferrite containing fine Fe 3 C particles. Alloying with about 1.5wt% of silicon suppresses the precipitation of Fe 3 C during the bainite transformation and the resulting microstructure of these silicon-rich carbidefree steels consists of fine plates of α separated by carbon-enriched regions of γ. These carbide-free bainitic steels show exceptional promise as rail steels, since the brittle Fe 3 C phase is eliminated; they derive their strength from the ultrafine α plates, which are much less than 1 µm in thickness. Such grain refinement simultaneously improves both the strength and the toughness of steel and these steels are relatively cheap to produce. They, therefore, show considerable potential in terms of reduced maintenance and increased safety with an expected reduction in rail fractures. Maraging steels Maraging steels may be termed ultra-high-strength steels and may exhibit
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Materials for engineering Third edi
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Woodhead Publishing Limited and Man
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vi Contents 3.4 Degradation of meta
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Preface to the third edition The cr
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Preface to the first edition This t
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xvi Introduction Young’s modulus,
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1 Structure of engineering material
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Structure of engineering materials
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1.2 Microstructure Structure of eng
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1.4 Further reading Structure of en
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Part III Problems
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Appendix I Useful constants Symbol
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234 Appendix II Fracture toughness
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Appendix IV Sources of material pro
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Sources of material property data 2
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Index acrylics 160 adhesives 121 ad
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Index 245 smart fibre 189 stiffness
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Index 247 GPC (gel permeation chrom
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Index 249 offset yield strength 39
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Index 251 nitriding 83-4 normalisin
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Materials for engineering, 3rd Edition - (Malestrom)

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