US3178279A - Nitride bearing low-manganese ductile steel - Google Patents

Nitride bearing low-manganese ductile steel Download PDF

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Publication number
US3178279A
US3178279A US189211A US18921162A US3178279A US 3178279 A US3178279 A US 3178279A US 189211 A US189211 A US 189211A US 18921162 A US18921162 A US 18921162A US 3178279 A US3178279 A US 3178279A
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steel
lmn
manganese
aluminum
low
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US189211A
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Nakamura Hajime
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IHI Corp
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IHI Corp
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    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium

Definitions

  • the object of the present invention to provide low-Mn steels having refined and uniform granular structure, which are best suited for serving as structural steels at low temperatures.
  • the low-Mn steel of the present invention exhibits markedly improved ductility due to the presence of appropriate amounts of aluminum nitride as a precipitate, it is in practice not feasible to provide the accurate amounts of aluminum and nitrogen needed for the formation of the desired amounts of aluminum nitride. In every case in practice, either nitrogen or aluminum will be in excess with respect to the other component.
  • the invention therefore, has for its object to minimize 3,178,279 Patented Apr. 13, 1965 the detrimental effect of metallic aluminum, by keeping the ratio between aluminum and aluminum nitride at a specified value, and by keeping the free nitrogen content under 0.004% by Weight.
  • the present invention relates to low-Mn grade steels containing about 0.05 to 0.25% carbon, less than about 0.60% silicon, about 1.00 to 2.50% manganese, which are characterized by a component consisting of about 0.03 to 0.12% precipitated aluminum nitride, and a component consisting of about 0.003 to 0.15% dissolved metallic aluminium, as well as featuring the granular structure wherein the grain size is over No. 9 in terms of the ASTM ferrite grain size number system.
  • the invention further comprises steels of the composition containing 0.05-0.25 carbon, less than 0.60% silicon, 1.002.5% manganese, 0.030.12% precipitated aluminum nitride, 0.003-0.15% metallic aluminum in solid solution, and 1% of at least one of the elements of the group consisting of nickel, chromium, molybdenum, vanadium and copper, and less than 0.1% boron.
  • FIGS. 1 and 2 are drawings in which the transition temperature characteristics of various low-Mn grade steels are compared in terms of Charpy V-notch testing method
  • FIG. 3 is a drawing to show the relation between the amount of dissolved metallic aluminum in solid solution and the ferrite grain size
  • FIG. 4 is a drawing to show the relation between the amount of precipitated aluminum nitride and the ferrite grain size for various low-Mn grade steels with different amounts of dissolved metallic aluminum in solid solution,
  • FlGS. 5 and 6 are photomicrograms to show the granular structure of a low-Mn grade steel of the present invention.
  • the LMn 2 has a similar composition to LMn he aluminum is small. It will be further seen that, for 1 except for the carbon content which is slightly higher steels containing a large amount of dissolved metallic than in LMn l, and as a consequence, its tensile strengths aluminum, the necessary limitation imposed upon the conare of the order of 55 and 60 kg/mm. corresponding tent of precipitated aluminum nitride is over 0.10% or to mode of heat treatment of normalization or quench- 0.05% corresponding to the mode or" heat treatment of and-tempering, respectively.
  • LMn 3 is a similar steel. to normalization or quench-and-tempering, respectively. 7 LMn 1 except that its metallic aluminum component is It follows from those empirical findings described considerably higher than in LMn l, and the tensile above, and the fact that the cooling rates applied on specistrengths are almost equal to those of the latter.
  • LMn 4 mens involved in the various tests were rather faster than is again another Si-Mn type steel except modified by what would be realized in practice, a use of optimum small amounts of Ni, Cr, Mo and V each to improve the compositions ranging from about 0.03 to 0.12% for pretensile strengths which are of the order of 60 or '70 rripitated aluminum nitride, and from about 0.003 to kg./rnm. when normalized or quench-and-tempered, re- 0.15% for dissolved metallic aluminum in solid solution, spectively. is proper for successrul production of fine-grained, low- Steels designated as LMn A, LMn B and LMn C are temperature ductile low-Mn grade steels.
  • low-Mn grade steels that were acquired from 4Q;
  • FIG. 2 the transition temperature characteristics of commercial market.
  • the LMn A is equivalent to LMn two different low-Mn grade steels, as normalized, one due 2, LMn B to LMn l, and LMn C to LMn 4, respectively.
  • the LMn 4 and the other a com-
  • the transition temperature curves obtained from lowmercial steel, the LMn C are compared. It is to be seen Mn grade stels of the present invention and those from that the steel of the present invention is far more ductile commercial steels of the same grade are compared in than its commercial counterpart as evidenced by the rela- FIG. 1.
  • the low-Mn tive position or" the transition temperature curves the one grade steels containing precipitated aluminum nitride of representing the steel to in accordance with the present more than 0.03% all have transition temperature curves invention lying at far lower side in the temperature scale that are in a temperature region that is lower by about and far above along the impact value scale with respect 40 to 80 C. as compared with those of commercial to the commercial steel. counterparts, and, moreover, the absorbed energy at frac- FIGS. 5 and 6 are photomicrograms showing the microture in the former varieties is far larger than that in the structure of a low-Mn grade steel of the present invention, latter at any temperature tested. the LMn 1.
  • the grain size thereof is It will be noted in FIG. 1, furthermore, that the transiabout No. 12 in terms of the ASTM ferrite grain size tion temperature curves of LMn 3 is shifted towards the system, higher t m t side with f to flfose of LMn
  • the low-Mn grade steels due to the present invention The i shlft of the curve and about are all heat-treatable in that the granular structure thereof for h .3.
  • Propernum nitride is about 800 C. to 1050 C., whereafter g gi ii g g g gi izgifiigfi g ggg i t i fi gii f V the steel is rapidly cooled in a fluid medium to retain the While FIG. 4 Shows a relation between ferrite grain state of preclpitationh to tlge fullest extent. if desired, size and amount of precipitated aluminum nitride for me Steel may be furt er Su jected to a tempering Stgp at a temperature between about C. and 750 C.
  • a nitride bearing low manganese ductile steei consisting essentially of, by weight, 0.05% to 0.15% carbon, less than.0.60% silicon, 1.0% to 2.5% manganese, 0.03%
  • a nitride bearing low manganese ductile steel consisting essentially of, by weight, 0.05% to 0.15% carbon, less than 0.60% silicon, 1.0% to 2.5% manganese, 0.03% to 0.12% precipitated aluminum nitride, 0.003% to 0.15% metallic aluminum in solid solution, less than 1% of at least one element selected from the group consisting of nickel, chromium, molybdenum, vanadium, and copper, less than 0.1% boron, balance iron with incidental impurities said steel having a grain size finer than number 9 in terms of the ASTM ferrite grain size numbering system.
  • Method for the heat treatment of steel having a chemical composition according to claim 1, comprising the steps of heating said steel to a temprature between about 800 and 1050" C. for maximum precipitation of aluminum nitride, and then cooling the steel rapidly in a fluid medium to retain the state of precipitation of the nitride to the fullest extent.
  • Method for the heat treatment of steel having a chemical composition according to claim 2 comprising the steps of heating said steel to a temperature between about 800 and 1050 C. for maximum precipitation of aluminum nitride, and then cooling the steel rapidly in References Cited by the Examiner UNITED STATES PATENTS 2,679,454 5/54 Ofienhauer -128.5

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
US189211A 1961-05-16 1962-04-20 Nitride bearing low-manganese ductile steel Expired - Lifetime US3178279A (en)

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Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3258372A (en) * 1963-01-21 1966-06-28 Int Nickel Co Martensitic low alloy plate steel
US3320099A (en) * 1964-08-12 1967-05-16 United States Steel Corp Method of processing steel
US3357822A (en) * 1964-06-26 1967-12-12 Sumitomo Metal Ind Low-carbon aluminum killed steel for high temperature applications
US3807990A (en) * 1968-09-11 1974-04-30 Nippon Steel Corp Low-alloy high-tensile strength steel
US4042273A (en) * 1975-05-20 1977-08-16 Fried. Krupp Huttenwerke Ag Rail wheel
CN106702392A (zh) * 2015-07-15 2017-05-24 昆山鑫昌泰模具科技有限公司 Qt-600球墨铸铁的链接臂与转向盘加工工艺

Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2679454A (en) * 1952-02-08 1954-05-25 Union Carbide & Carbon Corp Article for low-temperature use
GB808556A (en) * 1954-05-17 1959-02-04 Mannesmann Ag A process for the heat treatment of an unalloyed or low-alloy structural steel containing from 0.03% to 0.12% of aluminium nitride

Patent Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2679454A (en) * 1952-02-08 1954-05-25 Union Carbide & Carbon Corp Article for low-temperature use
GB808556A (en) * 1954-05-17 1959-02-04 Mannesmann Ag A process for the heat treatment of an unalloyed or low-alloy structural steel containing from 0.03% to 0.12% of aluminium nitride

Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3258372A (en) * 1963-01-21 1966-06-28 Int Nickel Co Martensitic low alloy plate steel
US3357822A (en) * 1964-06-26 1967-12-12 Sumitomo Metal Ind Low-carbon aluminum killed steel for high temperature applications
US3320099A (en) * 1964-08-12 1967-05-16 United States Steel Corp Method of processing steel
US3807990A (en) * 1968-09-11 1974-04-30 Nippon Steel Corp Low-alloy high-tensile strength steel
US4042273A (en) * 1975-05-20 1977-08-16 Fried. Krupp Huttenwerke Ag Rail wheel
CN106702392A (zh) * 2015-07-15 2017-05-24 昆山鑫昌泰模具科技有限公司 Qt-600球墨铸铁的链接臂与转向盘加工工艺
CN106702392B (zh) * 2015-07-15 2019-11-29 昆山鑫昌泰模具科技有限公司 Qt-600球墨铸铁的链接臂与转向盘加工工艺

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BE614882A (fr) 1962-07-02

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