US3692591A - Method for effecting the rapid heat-treatment of steel plate - Google Patents

Method for effecting the rapid heat-treatment of steel plate Download PDF

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Publication number
US3692591A
US3692591A US68205A US3692591DA US3692591A US 3692591 A US3692591 A US 3692591A US 68205 A US68205 A US 68205A US 3692591D A US3692591D A US 3692591DA US 3692591 A US3692591 A US 3692591A
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United States
Prior art keywords
temperature
steel
treatment
rapid
heating
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Expired - Lifetime
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US68205A
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English (en)
Inventor
Donald S Dabkowski
Lew F Porter
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United States Steel Corp
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United States Steel Corp
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/78—Combined heat-treatments not provided for above

Definitions

  • This invention relates to a method for preconditioning steel plates so that they may be effectively heat-treated to produce an unusually fine-grained structure.
  • variable frequency sources at the power levels required, are not commercially available, and since the optimum frequency for maximum heating at the midthickness of a plate is different for each plate thickness; in a practical commercial system, a compromise frequency would be required, e.g. one that offers reasonably uniform heating for the various thicknesses employed; (b) the depth of penetration of a given frequency (shown below) is much lower below the curie temperature of the steel, than above the curie temperature (about 1250 F.)
  • FIG. 1, A, B, C, and D illustrates the effect of initial grain structure on the degree of grain refinement which can be achieved after only one cycle of rapid austenitization.
  • FIG. 2 is a graph illustrating the effect of preconditioning time on the physical properties of a cyclicly heattreated steel.
  • a 1-inch thick plate of a 5 Ni-Cr-Mo-V steel was rapidly austenitized (see Table II for chemical analysis) at 16 F./second to 1500 F. and then Water quenched. The cycle was repeated five times (e.g. the method of US. Pat. No. 3,178,324) after which the plate was tempered at 400 F. for one hour. The mid-thickness physical properties of the resultant product are reported in FIG. 2, at time.
  • a series of the same steels were similarly rapidly austenitized at 16 F./ second to 1500 F., water quenched and reheated for five cycles, except that prior to each rapid austenitizing treatment, the plates were preconditioned at 115 0 F.
  • preconditioning for various time periods. While all periods (within the reported times) of preconditioning would appear to effect at least some enhancement in properties, it may be seen in FIG. 2, that preconditioning for a time of about to 30 minutes will provide a significant increase in strength and ductility. Although conditioning for longer than about 30 minutes will not seriously decrease properties, such longer times are less desirable in that they are uneconomical.
  • the preheat treatment of this invention will also aid in eliminating excessive temperature differences between the midthickness and the surface of heavy plate or pipe sections.
  • Steel plates see Table II, for chemical analysis
  • two inches thick were rapidly austenitized (without a preheat) by induction heating at a frequency of 960 c.p.s. (this frequency represents the best compromise for midthickncss heating of plates from /2 through 3 inches thick).
  • Example a when the surface of the plate was heated to optimum peak temperature, the temperature of the midthickness of the plate was below the A temperature (1415 F. for this composition) of the steel. Thus, the midthickness was not completely austenitized and therefore did not achieve full grain refinement, resulting in a smaller improvement in yield strength than the plate surface. Likewise (Example b), when the midthickness was heated to optimum peak temperature, the surface temperature became so high that grain coarsening resulted, along with its consequent loss in yield strength.
  • the preconditioning treatment of the present invention will therefore provide a plate product with substantially uniform properties throughout the thickness, a uniformity which would otherwise be unobtainable employing the fast heat-up rates (from room temperature) re quired for effective grain refinement.
  • a method of producing ultra-fine grains in a steel product which method consists of employing at least one cycle in which the steel is rapidly heated to above its A temperature for a time just sutficient to transform it to an austenitic structure, and is then immediately cooled at a rate equal to or greater than that required to transform the austenite to a fine grained ferrite-pearlite aggregate, the improvement which comprises preconditioning said steel by preheating at a temperature in the range of from (A -150) F. to a temperature just below the A temperature of the steel, for a time of about 5 minutes to about 30 minutes, prior to each of the rapid heating cycles employed.
  • a method of producing ultra-fine grains in steel products having a thickness of from about /2 inch to 3 inches which method consists of employing at least one cycle in which the steel is rapidly heated to above its A temperature for a time just suflicient to transform it to an austenitic structure, and is then immediately cooled at a rate equal to or greater than that required to transform the austenite to a fine grained ferrite-pearlite aggregate, the improvement which comprises preconditioning said steel by preheating the steel at a temperature in the range of from (A -150T F. to a temperature just below the A temperature of the steel, for a time at least sutficient to substantially equalize the temperature of the surface with that of the midthickness of the product, prior to each of the rapid heating cycles employed.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
  • Heat Treatment Of Steel (AREA)
US68205A 1970-08-31 1970-08-31 Method for effecting the rapid heat-treatment of steel plate Expired - Lifetime US3692591A (en)

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US6820570A 1970-08-31 1970-08-31

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US (1) US3692591A (enExample)
AU (1) AU456306B2 (enExample)
BE (1) BE771962A (enExample)
BR (1) BR7105663D0 (enExample)
CA (1) CA938535A (enExample)
DE (1) DE2143611A1 (enExample)
ES (1) ES394653A1 (enExample)
FR (1) FR2106124A5 (enExample)
GB (1) GB1342417A (enExample)
IT (1) IT939765B (enExample)
NL (1) NL7111983A (enExample)
SE (1) SE365552B (enExample)
ZA (1) ZA715619B (enExample)

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3855013A (en) * 1972-03-07 1974-12-17 Licencia Talalmanyokat Quick heat treatment of steels
US5666045A (en) * 1994-12-09 1997-09-09 Psc Inc. Laser drive and control systems useful for laser diode protection
US20120118441A1 (en) * 2009-08-21 2012-05-17 Sumitomo Metal Industries, Ltd. Method of manufacturing heavy-wall seamless steel pipe
WO2017114599A1 (en) * 2015-12-30 2017-07-06 Robert Bosch Gmbh Method for manufacturing steel transverse elements for a drive belt for a continuously variable transmission
CN109762965A (zh) * 2019-02-01 2019-05-17 哈尔滨工业大学（威海） 一种超高强韧性Mn-B钢结构件连续在线制备方法

Families Citing this family (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
AU537333B2 (en) * 1979-11-09 1984-06-21 La Salle Steel Co. Process for annealing steels
FR2594145B1 (fr) * 1986-02-13 1992-06-12 Stein Heurtey Procede de traitements mecaniques et thermochimiques des metaux
CN104611533A (zh) * 2015-02-06 2015-05-13 桂林理工大学 一种细化35号钢奥氏体晶粒的加热方法
CN104611531A (zh) * 2015-02-06 2015-05-13 桂林理工大学 一种细化45号钢奥氏体晶粒的加热方法
CN104611529A (zh) * 2015-02-06 2015-05-13 桂林理工大学 一种细化75号钢奥氏体晶粒的加热方法
CN104611527A (zh) * 2015-02-06 2015-05-13 桂林理工大学 一种细化65号钢奥氏体晶粒的加热方法

Cited By (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3855013A (en) * 1972-03-07 1974-12-17 Licencia Talalmanyokat Quick heat treatment of steels
US5666045A (en) * 1994-12-09 1997-09-09 Psc Inc. Laser drive and control systems useful for laser diode protection
US20120118441A1 (en) * 2009-08-21 2012-05-17 Sumitomo Metal Industries, Ltd. Method of manufacturing heavy-wall seamless steel pipe
CN102482727A (zh) * 2009-08-21 2012-05-30 住友金属工业株式会社 厚壁无缝钢管的制造方法
US8845830B2 (en) * 2009-08-21 2014-09-30 Nippon Steel & Sumitomo Metal Corporation Method of manufacturing heavy-wall seamless steel pipe
EP2468904A4 (en) * 2009-08-21 2016-03-23 Nippon Steel & Sumitomo Metal Corp METHOD FOR PRODUCING A THICK WOVEN, SEAMLESS STEEL TUBE
WO2017114599A1 (en) * 2015-12-30 2017-07-06 Robert Bosch Gmbh Method for manufacturing steel transverse elements for a drive belt for a continuously variable transmission
NL1041655B1 (en) * 2015-12-30 2017-07-11 Bosch Gmbh Robert Method for manufacturing steel transverse elements for a drive belt for a continuously variable transmission.
CN108474450A (zh) * 2015-12-30 2018-08-31 罗伯特·博世有限公司 用于制造用于无级变速器的驱动带的钢制横向元件的方法
JP2019510131A (ja) * 2015-12-30 2019-04-11 ローベルト ボツシユ ゲゼルシヤフト ミツト ベシユレンクテル ハフツングＲｏｂｅｒｔ Ｂｏｓｃｈ Ｇｍｂｈ 連続可変トランスミッション用の駆動ベルト用の鋼製の横断要素の製造方法
CN109762965A (zh) * 2019-02-01 2019-05-17 哈尔滨工业大学（威海） 一种超高强韧性Mn-B钢结构件连续在线制备方法
CN109762965B (zh) * 2019-02-01 2024-04-16 哈尔滨工业大学（威海） 一种超高强韧性Mn-B钢结构件连续在线制备方法

Also Published As

Publication number Publication date
AU3270571A (en) 1973-03-01
DE2143611A1 (de) 1972-03-09
NL7111983A (enExample) 1972-03-02
SE365552B (enExample) 1974-03-25
BR7105663D0 (pt) 1973-05-17
AU456306B2 (en) 1974-12-12
BE771962A (fr) 1972-02-29
IT939765B (it) 1973-02-10
CA938535A (en) 1973-12-18
ZA715619B (en) 1972-04-26
GB1342417A (en) 1974-01-03
ES394653A1 (es) 1974-09-16
FR2106124A5 (enExample) 1972-04-28

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Owner name: USX CORPORATION, A CORP. OF DE, STATELESS

Free format text: MERGER;ASSIGNOR:UNITED STATES STEEL CORPORATION (MERGED INTO);REEL/FRAME:005060/0960

Effective date: 19880112