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Series: ASM Handbook
Volume: 4A
Publisher: ASM International
Published: 01 August 2013
DOI: 10.31399/asm.hb.v04a.a0005774
EISBN: 978-1-62708-165-8
... Abstract Intensive quenching (IQ) is an alternative method of hardening steel parts, providing extremely high cooling rates within the martensite-phase formation temperature range. This article begins with the description on the general correlation between steel mechanical properties...
Abstract
Intensive quenching (IQ) is an alternative method of hardening steel parts, providing extremely high cooling rates within the martensite-phase formation temperature range. This article begins with the description on the general correlation between steel mechanical properties and cooling rate during IQ. It presents a review of batch intensive quenching (IQ-2) methods and single-part intensive quenching (IQ-3) methods as well as practical applications of these methods. The article provides useful information on the effect of heat flow on cooling in these methods, and discusses the improvements achieved in part microstructure, mechanical properties, and stress conditions of steel, after intensive quenching. It also describes the reasons for part distortion in IQ, and reviews the types of quench systems used in IQ-2 and IQ-3 processes.
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Published: 01 December 2008
Fig. 1 Two applications of Replicast steel parts. (a) CF-8M stainless steel 150 mm (6 in.) butterfly valve body. The part is approximately 305 mm (12 in.) in outside diameter, 64 mm (2 1 2 in.) thick, and weighs 11 kg (25 lb). Note as-cast bolt holes and O-ring groove. (b) 8640 steel
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Published: 01 January 2002
Fig. 12(a) Two AISI A6 tool steel parts that shattered during finish (abusive) grinding. See also Fig. 12(b)
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Published: 01 January 1994
Fig. 12 Times required for interfaces of two steel parts of equal area but different mass to reach baking temperature of 150 °C (300 °F)
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Published: 01 December 1998
Fig. 43 Effect of repressing pressure on porosity of 316L stainless steel parts pressed from 4 to 8 tonnes/cm 2 and presintered for 15 min at 1050 °C (1920 °F). Source: Ref 10
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Published: 30 August 2021
Fig. 12 (a) Two AISI A6 tool steel parts that shattered during finish (abusive) grinding. (b) Micrograph of the ground parts showing a reaustenitized region (white) and a back-tempered zone (dark) at the ground surface. Etched with 3% nital. Original magnification: 70×
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Published: 30 September 2014
Fig. 6 Recovery rates for 25 mm (1 in.) diameter steel parts in a 0.3 m 3 (10 ft 3 ) fluidized-bed furnace
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Published: 01 November 2010
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Published: 01 November 2010
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Published: 15 June 2020
Fig. 13 Optical micrographs of 17-4 PH stainless steel parts fabricated using various powders by LPBF at an energy density 104 J/mm 3 , before and after HIP treatment
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Published: 15 June 2020
Fig. 14 Tafel plots of 17-4 PH stainless steel parts fabricated with various powders by LPBF at an energy density 104 J/mm 3 , before and after HIP treatment.
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Published: 01 January 2005
Fig. 27 Deep pitting attack was discovered on steel bolts used to retain parts in a metal-shaping (cutting) machine. The surfaces of the bolts were covered with a black, oily substance, which, on analysis, was found to contain sulfurous species. Other steel parts also failed by pitting attack
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Published: 01 January 2006
Fig. 8 Parts with holes punched by P/M tool steels. Parts include: punching of fine slots in brass parts for clocks; punching of 3 mm (0.118 in.) holes in high-carbon steel (0.7% C) sheet (240 HB); punching of holes in chain links made of 0.55% carbon steel with a thickness of 2 mm (0.079
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Published: 01 January 2002
Fig. 14 Fatigue failure of a low-alloy steel part. Shear lips around most of the periphery (as at arrows) as well as chevron marks over most of the fracture surface aid in identifying the fatigue fracture area at the lower left corner. Source: Ref 15
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Published: 01 January 2002
Fig. 16 Beach marks on a 4340 steel part caused by SCC. Tensile strength of the steel was approximately 1780 to 1900 MPa (260 to 280 ksi). The beach marks are a result of differences in the rate of penetration of corrosion on the surface. They are in no way related to fatigue marks. 4×
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Published: 01 January 2002
Fig. 3 Surface of a fatigue fracture in a 4330V steel part. Chevron marks point to origin of fatigue in lower left corner. Arrows identify shear rupture along the periphery.
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Published: 01 December 2004
Fig. 21 Beach marks on a 4340 steel part caused by stress-corrosion cracking. Tensile strength of the steel was approximately 1780 to 1900 MPa (260 to 280 ksi). The beach marks are a result of differences in the rate of penetration of corrosion on the surface. They are in no way related
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in Metallography and Microstructures of Powder Metallurgy Alloys
> Metallography and Microstructures
Published: 01 December 2004
Fig. 27 Insufficiently sintered 316L stainless steel part showing original particle boundaries and sharp, angular pores. As-polished cross section. Part sintered for 30 min at 1093 °C (2000 °F) in H 2 . Courtesy of OMG Americas
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Published: 15 January 2021
Fig. 14 Fatigue failure of a low-alloy steel part. Shear lips around most of the periphery (as at arrows) as well as radial marks over most of the fracture surface aid in identifying the fatigue fracture area at the lower left corner. Source: Ref 15
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Published: 15 January 2021
Fig. 24 Beach marks on a 4340 steel part caused by stress-corrosion cracking. Tensile strength of the steel was approximately 1780 to 1900 MPa (260 to 280 ksi). The beach marks are a result of differences in the rate of penetration of corrosion on the surface. They are not related to fatigue
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