US3048505A - Process of prehardening austenitic manganese steel - Google Patents

Process of prehardening austenitic manganese steel Download PDF

Info

Publication number
US3048505A
US3048505A US833344A US83334459A US3048505A US 3048505 A US3048505 A US 3048505A US 833344 A US833344 A US 833344A US 83334459 A US83334459 A US 83334459A US 3048505 A US3048505 A US 3048505A
Authority
US
United States
Prior art keywords
steel
temperature
austenitic
heating
hardness
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Expired - Lifetime
Application number
US833344A
Other languages
English (en)
Inventor
Herbert C Doepken
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Manganese Steel Forge Co
Original Assignee
Manganese Steel Forge Co
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Manganese Steel Forge Co filed Critical Manganese Steel Forge Co
Priority to US833344A priority Critical patent/US3048505A/en
Priority to GB23516/60A priority patent/GB941828A/en
Priority to BE593518A priority patent/BE593518A/fr
Priority to LU39047D priority patent/LU39047A1/xx
Application granted granted Critical
Publication of US3048505A publication Critical patent/US3048505A/en
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
    • C21D6/00—Heat treatment of ferrous alloys

Definitions

  • the Hadfield composition it is convention al practice to vary this composition somewhat, as by varying the proportions given in his formula (for example, the carbon may be in the range of 0.65% to 1.40%, or the silicon may be 2.00%), or by adding supplementary ingredients such as nickel, chromium, vanadium, or molybdenum. But regardless of such changes, the steel does not lose its identity as Hadfield-type-steel which is austenitic and non-magnetic, and the problem of hardening is still present in all these forms regardless of whether the material is cast or wrought.
  • Such a manganese steel composition isnorrnally heattreated by raising the temperature above the upper critical point until it becomes completely austenic and then quenching it in water. This temperature varies from 1800 to 1900 F. After this heat treatment, the material remains essentially austenitic. In this condition the material has approximately a yield strength of 55,000 to 75,000 p.s.i., an ultimate strength of 135,000 to 165,000 p.s.i., and an elongation of 35% to 60%.
  • Such austenitic steel is inherently ductile to a high degree but lacks desired hardness since its hardness is usually only 180 to 215 Brinell.
  • austenitic manganese steel attains its long-wearing characteristics
  • work-hardening in use. Impact on manganese steel increases the surface hardness to about 450 to 600 Brinell, depending on the severity of the impact. The depth of work-hardening also increases wtih increasing severity of impact. For a great number of heavy duty operations, this work-hardened material is compl tely satisfactory and outwears any other material.
  • the present invention starts with austenite (which is inherently ductile but lacks desired hardness) and modifies it in essential particulars, first, by prehardening it (with accompanying loss of ductility) and then by reclaiming apart only of the original ductility without sub Turning now to the drawing, there is shown a firstheating zone 1, a cooiing zone .2, a second-heating zone 3, and a quenching zoned.
  • austenitic 10.00% to 14.00% manganese steel is delivered to the first-heating zone 1, and there uniformly heated at a carefully-controlled predetermined degree of temperature, which i uniformly maintained, for a suflicient length of time to develop an acicular structure having carbide needles within the grains of the steel but with the boundaries of the grains being comparatively free of carbide precipitation.
  • the steel is then delivered to cooling zone 2 where it is slowly cooled to ambient temperature.
  • cooling zone 2 the steel is slowly cooled to ambient temperature. Satisfactory. results have been obtained when the cooling has lasted for a period of time between 10 to 48 hours.
  • zone 4- for immediate quenching in water.
  • the steel is heated to a temperature in the range of 1350 F. to 1500 F. to a prepartially dissolved to the extent of removing their sharppoints and making the needles smaller and of approximately the shape of little round balls.
  • These balls are just as hard as the needles, but because the balls are surrounded by ductile material, and because the sharp points of the needles have been eliminated, the steel has regained adequate ductility, that is, a part only of its original ductility sufficient to resist heavy impact in use. This is effected without substantial loss of the hardness imparted to the steel in the first-heating step.
  • the steel is subjected to the heat of the second-heating zone 3, which is maintained uniformly, for a period of time of not less than two hours, after which the steel is quickly quenched.
  • This quenching is preferably accornplished by immersing the steel in water.
  • the Brinell hardness of the resulting product may be controlled by controlling the temperature of the second- I heating zone 3. For example, it has been found that subjecting the steel in the second-heating zone 3 to a temperature of 15 F. gives the resulting product a hardness of 300 Brinell, subjecting the steel in second-heating zone 3 to a temperature of 1450 F. gives a hardness of 350 delivered to cooling zone 2 where it is slowly cooled for a period of ten hours to ambient temperature.
  • the plate is delivered to second-heating zone 3 wherein it is subjected to a predetermined uniform temperature of substantially 1400 F. which is maintained uniformly'for two hours. quenched by transferring it to quenching zone 4 and submerging it in water. The resulting hardness of the plate was found to be 400 Brinell.
  • the fully austenitic rolled steel is heated to a temperature of 1200 P. which is maintained uniformly in first-heating zone It for a sufiicient length of time to develop an acicular structure having precipitated carbide needles within the grains of the steel. This structure forms uniformly within the grains, with some carbide precipitation forming on the grain boundaries but not in unwanted concentrations.
  • Example 1 A rolled-steel plate, such as is used by many asphalt plants for asphalt mixer liners, formed of fully austenitic 10.00% to 14.00% manganese steelis subjected to the process of this invention.
  • This plate is delivered to firstheating zone 1, and is subjected to a predetermined tem perature of substantially 1200 F. which is maintained uniformly for about 'six hours. After this, the rolledsteel plate is delivered to the coolingzone 2 where it is cooled slowly to ambient temperature for a period of ten hours.
  • the steel plate is delivered to second-heating zone 3 where it is heated'to a predetermined temperature of substantially 1450 P. which is maintained uniformly for two hours.
  • the steel is delivered to quenching
  • the processed plate was found to have a hardness of 350 Brinell.
  • Example 2 V A rolled-steel plate, such as is used by the automobile industry for shot blast liners, formed of fully austenitic 10.00% to 14.00% manganese steel, is subjected to the process of this invention.
  • the plate is delivered to firstheating zone 1 wherein it is subjected to a predetermined uniform temperature of substantially 1200 P. which is maintained uniformly for about six hours. Then the plate is delivered to cooling zone 2. where itis slowly cooled for ten hours to ambient temperature.
  • the steel plate is delivered to heating zone 3 wherein it is subjected to a predetermined uniform temperature of substantially 1500 P. which is maintained Next, it is immediately quenched by being delivered to quenching zone 4- and submerged in water.
  • the resulting hardness of the plate was found to be 300 Brinell.
  • the plate for blast furnace bell liners, is formed of fully austenitic 10.00% to 14.00% manganese steel.
  • the plate is subjected to the process of this invention by delivering it to heating zone Lwhere it is subjected to a predetermined uniform temperature of approximately 1200 P. which is maintained uniformly for siX hours. Then the plate is temperature range of such first heat.
  • the second heat treatment is then applied to the steel in second-heating zone 3.
  • a two-hour soak at 1450 F. (as in Example 1) is foundto be satisfactory. After this soak, the material is immediately water-quenched from that temperature.
  • the purpose of the second heating is to partially dis solve the carbides by dissolving the sharp edges only of the acicular structure developed in the first-heating zone, thereby leaving an austenitic matrix with carbide precipitates uniformly distributed throughout the grains. These carbides are round or oblong with nosharp edges.
  • the purpose of this second heating is not to establish an austenitic structure, nor is its purpose to dissolve carbides completely.
  • the purpose of the second heating is only to sufliciently dissolve the sharp edges from each carbide precipitate in order to restore ductility without reducing hardness.
  • Yield strength 120,000 to 140,000 p.s.i., Ultimate strength, 135,000 to 165,000 p.s.i., Elongation in 2 inches, 10% to 16%.
  • the material has a hardness which may be varied from 300 to 400 Brinell.
  • the material may be work-hardened in use to 450 to 600 Brinell. In all cases, the desired adequate ductility is retained in the material.
  • a process of prehardening austenitic manganese steel to form a steel of superior hardness and ductility comprising heating austenitic manganese steel to a temperature above that at which ferrite goes into solution in the austenitic matrix and below the temperature at which carbide fully dissolves into the austenitic matrix, in order to precipitate carbide needles within the grains of the steel, allowing the steel to cool to ambient temperature, heating the steel to a higher temperature than that in the first said heating step but within the first said heating range, in order to diminish the size and round oit the sharp points of said carbide needles, and quenching the steel.
  • a process of prehardening austenitic manganese steel to form a steel of superior hardness and ductility comprising the steps of heating austenitic manganese steel to a temperature in the range between 1100 F. to 1300 F. to precipitate carbide needles within the steel, allowing the steel to cool to ambient temperature, heating the steel to a temperature in the range of 1350 F. to 1500 F. to diminish the size and round ofi sharp points of the carbide needles, and quenching the steel.
  • a process of prehardening 10.00% to 14.00% manganese steel before use to form a steel of superior hardness and ductility comprising heating said steel at approximately 1200" F. and uniformly maintaining the temperature for about six hours to develop an acicular structure having needles within the grains but with the boundaries of the grains being comparatively free of varbide precipitation, slowly cooling said steel for 10 to 48 hours to ambient temperature, heating the steel to a temperature of about 145 0 F. and uniformly maintaining the temperature for at least two hours to diminish the size and round off sharp points of said needles, and then water-quenching said steel, whereby to form a prehardened manganese steel.
  • a process of prehardening 10.00% to 14.00% manganese steel before use to form a steel of superior hardness and ductility and a Brinell hardness of substantially 300 comprising heating said steel at approximately 1200 F. and uniformly maintaining the temperature for about six hours to develop an acicular structure having needles within the grains but with the boundaries of the grains being comparatively free of carbide precipitation, slowly cooling said steel for 10 to 48 hours to ambient temperature, heating the steel to a temperature of about 1500 F. and uniformly maintaining the temperature for at least two hours to diminish the size and round off sharp points of said needles, and then water-quenching said steel, whereby to form a prehardened manganese steel with a Brinell hardness of substantially 300.
  • a process of prehardening 10.00% to 14.00% manganese steel before use to form a steel of superior hardness and ductility and a Brinell hardness of substantially 400 comprising heating said steel at approximately 1200 F. and uniformly maintaining the temperature for about six hours to develop an acicular structure having needles within the grains but with the boundaries of the grains being comparatively free of carbide precipitation, slowly cooling said steel for 10 to 48 hours to ambient temperature, heating the steel to a temperature of substantially 1400" F. and uniformly maintaining the temperature for at least two hours to diminish the size and round ofi sharp points of said needles, and then water quenching said steel, whereby to form a prehardened manganese steel with a Brinell hardness of substantially 400.
  • a process of prehardening before use austenitic 10.00% to 14.00% manganese steel, having carbon in the range of 1.00% to 1.40%, to form a steel of superior hardness and ductility consisting of heating said manganese steel at approximately 1200 F. and uniformly maintaining the temperature for about six hours, slowly cooling said steel for 10 to 48 hours to ambient tempera ture, heating the steel to a temperature of about 1450 F. and uniformly maintaining the temperature for at least two hours, and then water-quenching said steel, whereby to form a prehardened manganese steel.
  • P-rehardened austenitic manganese steel having a composition which includes carbon 0.65% to 1.40%, manganese 10.00% to 14.00%, phosphorus up to 0.10%, sulphur 0.01% to 0.03%, silicon 0.10% to 2.00%, said steel being non-magnetic and having an elongation in two inches of 10% to 16%, a hardness in the range of 300 to 400 Brinell, and an austenitic matrix with rounded carbide particles dispersed therethrough.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
US833344A 1959-08-12 1959-08-12 Process of prehardening austenitic manganese steel Expired - Lifetime US3048505A (en)

Priority Applications (4)

Application Number Priority Date Filing Date Title
US833344A US3048505A (en) 1959-08-12 1959-08-12 Process of prehardening austenitic manganese steel
GB23516/60A GB941828A (en) 1959-08-12 1960-07-05 Improvements in or relating to a process of prehardening austenitic manganese steel
BE593518A BE593518A (fr) 1959-08-12 1960-07-28 Procédé de prédurcissement d'un acier austénitique à forte teneur en manganèse
LU39047D LU39047A1 (nl) 1959-08-12 1960-08-04

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
US833344A US3048505A (en) 1959-08-12 1959-08-12 Process of prehardening austenitic manganese steel

Publications (1)

Publication Number Publication Date
US3048505A true US3048505A (en) 1962-08-07

Family

ID=25264161

Family Applications (1)

Application Number Title Priority Date Filing Date
US833344A Expired - Lifetime US3048505A (en) 1959-08-12 1959-08-12 Process of prehardening austenitic manganese steel

Country Status (4)

Country Link
US (1) US3048505A (nl)
BE (1) BE593518A (nl)
GB (1) GB941828A (nl)
LU (1) LU39047A1 (nl)

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2490244A1 (fr) * 1980-09-15 1982-03-19 Abex Corp Alliage ferreux et son traitement thermique donnant des caracteristiques elevees en ce qui concerne en particulier la resistance a l'usage
US4627144A (en) * 1985-03-08 1986-12-09 Wescott Steel, Inc. Method of making pin with manganese steel shroud
US4629353A (en) * 1985-03-08 1986-12-16 Wescott Steel, Inc. Manganese steel shroud for pin
US5226791A (en) * 1990-09-29 1993-07-13 Mazda Motor Corporation Structure of a rotor shaft and method of making same
CN113862429A (zh) * 2021-09-28 2021-12-31 燕山大学 一种钢的高效预硬化方法及钢制工件

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US1427121A (en) * 1920-09-18 1922-08-29 American Manganese Steel Co Heat treatment of manganese steel
US1851903A (en) * 1930-02-06 1932-03-29 Taylor Wharton Iron & Steel Heat treatment of cold shaped manganese steel articles
US1975746A (en) * 1929-11-11 1934-10-02 Taylor Wharton Iron & Steel Method of transforming manganese steel

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US1427121A (en) * 1920-09-18 1922-08-29 American Manganese Steel Co Heat treatment of manganese steel
US1975746A (en) * 1929-11-11 1934-10-02 Taylor Wharton Iron & Steel Method of transforming manganese steel
US1851903A (en) * 1930-02-06 1932-03-29 Taylor Wharton Iron & Steel Heat treatment of cold shaped manganese steel articles

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2490244A1 (fr) * 1980-09-15 1982-03-19 Abex Corp Alliage ferreux et son traitement thermique donnant des caracteristiques elevees en ce qui concerne en particulier la resistance a l'usage
US4627144A (en) * 1985-03-08 1986-12-09 Wescott Steel, Inc. Method of making pin with manganese steel shroud
US4629353A (en) * 1985-03-08 1986-12-16 Wescott Steel, Inc. Manganese steel shroud for pin
US5226791A (en) * 1990-09-29 1993-07-13 Mazda Motor Corporation Structure of a rotor shaft and method of making same
CN113862429A (zh) * 2021-09-28 2021-12-31 燕山大学 一种钢的高效预硬化方法及钢制工件
CN113862429B (zh) * 2021-09-28 2023-03-03 燕山大学 一种钢的高效预硬化方法及钢制工件

Also Published As

Publication number Publication date
BE593518A (fr) 1960-11-14
GB941828A (en) 1963-11-13
LU39047A1 (nl) 1960-10-04

Similar Documents

Publication Publication Date Title
JPH04365816A (ja) 冷間加工用棒鋼線材の製造方法
US4457789A (en) Process for annealing steels
US3048505A (en) Process of prehardening austenitic manganese steel
US3337376A (en) Method of hardening hypereutectoid steels
KR102326245B1 (ko) 냉간압조용 선재 및 이의 제조방법
US3844844A (en) High toughness iron balls and process of making the same
US3895972A (en) Thermal treatment of steel
US2799602A (en) Process for producing stainless steel
US1660790A (en) Process of preparing alloy steel for die blocks and other purposes
US2881107A (en) Austempered, cold-finished steels
US3826694A (en) Thermal treatment of steel
JPS58141331A (ja) 鍛造製品の熱処理法
US2875109A (en) Method for the isothermal treatment of alloys after casting
US2201555A (en) Copper and copper base alloys
US2087766A (en) Method of making rolled products
US3732127A (en) Method of heat processing alloy steel to obtain maximum softness and uniformity
JPH02213416A (ja) 高延性棒鋼の製造方法
US3922181A (en) Thermal treatment of steel
US3444008A (en) Controlled atmosphere processing
US1972248A (en) Method of treating ferrous alloys
JPH0213004B2 (nl)
US3235413A (en) Method of producing steel products with improved properties
JP2756533B2 (ja) 高強度、高靭性棒鋼の製造方法
US746039A (en) Process of producing carbon-steel castings.
JPS6156268A (ja) 高靭性高張力鋼およびその製造法