US3574602A - High tension tough steel having excellent property resisting to delayed rupture - Google Patents

High tension tough steel having excellent property resisting to delayed rupture Download PDF

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US3574602A
US3574602A US690783A US3574602DA US3574602A US 3574602 A US3574602 A US 3574602A US 690783 A US690783 A US 690783A US 3574602D A US3574602D A US 3574602DA US 3574602 A US3574602 A US 3574602A
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Hisashi Gondo
Isao Kimura
Tuneyasu Watanabe
Mitsuo Honda
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Yawata Iron and Steel Co Ltd
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    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01J—ELECTRIC DISCHARGE TUBES OR DISCHARGE LAMPS
    • H01J40/00—Photoelectric discharge tubes not involving the ionisation of a gas
    • H01J40/02—Details
    • 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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron

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  • This invention relates to a high tension tough steel having excellent property resisting to delayed rupture, consisting of 0.05 to 0.80% C, 0.05 to 2.00% Si, 0.30 to 2.00% Mn, 0.05 to 6.00% Cr 0.01 to 0.30% Tr, 0.005 to 0.30% Zr, 0.5 to 0.008% B as basis elements at least one element selected from the group consisting of Sn, Sb and As, from the group consisting of Nb+Ta, W, Hf and Pd and further from the group consisting of Mo, Ni, V and Cu, balance being Fe and impurities
  • This invention relates to a high tension tough steel having an excellent property resisting to delayed rupture and a tensile strength of above 100 kg. mm.
  • the object of the present invention is to provide a low alloy high tension steel having strong resistance to delayed rupture and a tensile strength of above 100 kg./ mm. particularly to provide a steel material which can display a delayed rupture resistance far superior to any conventional steel material at such a high level of tensile strength as more than 130-140 kg./mm.
  • the steel of the present invention has the following chemical composition: that is, it is composed of 0.05 to 0.80 wt. percent C, 0.05 to 2.00 wt. percent Si, 0.30 to 2.00 wt. percent Mn, 0.05 to 6.00 wt. percent Cr, 0.01 to 0.30 Wt percent Ti, 0.005 to 0.30 wt. percent Zr, and 0.0005 to 0.008 wt. percent B as basic alloying elements and further at least one element selected from the group consisting of Sn, Sb and As in an amount of 0.03 to 0.50 wt. percent.
  • the object of the present invention can be better achieved, if there is further added to the steel having the above mentioned composition at least one element selected from the group consisting of Nb+Ta, W, Hf and Pd in an amount of less than 1.00 wt. percent in the case of Nb+Ta, less than 1.00 wt. percent in the case of W, less than 0.50 wt. percent in the case of Hf and less than 1.00 wt. percent in the case of Pd.
  • at least one element selected from the group consisting of Mo, Ni, V and Cu may be added to each of United States Patent Ofice 3,5745% Patented Apr.
  • the steel of the present invention is characterized in that by causing conventional steel materials of various kinds such as Cr steel, Cr-Mo steel, Cr-Mo-Ni steel, Si-Mn steel, Si-Mn-Cr steel and the like, which have been made high tension steels having a tensile strength of more than kg./mm.
  • C is added to a steel to impart the strength and hardenability required for the steel, but if the content of C exceeds 0.80 wt. percent, an improvement in the hardenability can no more be expected and there is further danger of the toughness being extremely reduced by the formation of free cementite. Therefore, the upper limit of C was specified as 0.80 wt. percent. On the other hand, if the content of C is too small, the formation of martensite at the time of heat treatment becomes difficult, and a sufficient strength can not be obtained even by subjecting the steel to a cold working. Therefore, the lower limit was specified as 0.05 wt. percent.
  • Si and Mn are elements necessary for deoxidation in the steel manufacturing process, but moreover effective for improving the hardenability and bettering the strength and toughness.
  • the upper limit for both elements was made 2.00 wt. percent respectively.
  • the lower limit of Si was specified as 0.05 Wt. percent.
  • the addition of Mn was determined as more than 0.30 wt. percent, because the elfect of Mn of improving the hardenability will be diminished and also the efiect of preventing damage caused by S during a hot working will be weakened, if the content of Mn is too small.
  • Ti, Zr, B, Sn, Sb and As are very elements, to which the marked improvement in the property resisting to delayed rupture of the steel of the present invention are attributed.
  • multiplex effects resulted from combining Ti, Zr, B and at least one element selected from the group consisting of Sn, Sb and As in proper amounts such an excellent eifect as can not easily be expected from sole effect of each of these elements can be displayed. How ever, as it was confirmed by the experiments that the addition of each of these elements exceeds a certain limit,
  • all the samples of the present invention A1 to A18 contain three of elements Ti, Zr and B in addition C, Si and Cr as the basic constituents.
  • the reference B1, B2, B7 which contain one of the above mentioned three elements show that by adding only one of these three elements the effect of preventing delayed rupture cannot be obtained.
  • A1, A2, A3, A13 and A14 of the present invention show that by the addition of at least one element selected from the group consisting of Sn, Sb and As the time up to the occurrence of delayed rupture can be prolonged by a large margin. Also for instance, the comparison of A4 with B4, or A to B5 demonstrates clearly the effect obtained by adding the elements selected from the group of Sn, Sb and As.
  • the samples A6, A7, A8, A11, A14, A15 and A18 show that by adding further at least one element selected from the group consisting of Nb-f-Ta, W, Hf and Pd the property resisting to delayed rupture can be all the more improved, which is particularly distinguished when comparing with the reference samples B4, B5, B6, B7, B9, B and B11 which contain at least one element selected from the group consisting of Mo, Ni, V.
  • Ni, Mo, Cu and V are known as elements which are also efiective for improving the strength, toughness or hardenability of steels. Even when the steel of the present invention contains these elements, however, it does not mean that the object of the present invention might be lost thereby.
  • At least one element selected from this group is preferable to be added in the following ranges: 0.05 to 5.00 wt. percent Ni, 0.05 to 1.00 wt. percent Mo, 0.005 to 1.00 wt. percent V and 0.03 to 0.50 wt. percent Cu. If more than these ranges, the corresponding eifects can not be expected, but less than these, no efiect can be obtained.
  • the steel of the present invention is particularly fit for use in the field where the phenomenon of delayed rupture raises a grave technical issue, for instance, for use as high tensile strength bolts, steel wires or bar steels for prestressed concrete or other structure steel materials or parts thereof, in which an extreme high tensile strength is required.
  • a high tension tough steel having excellent delayed rupture resisting properties consisting of 0.05 to 0.80 wt. percent C, 0.05 to 2.00 wt. percent Si, 0.30 to 2.00 wt. percent Mn, 0.05 to 6.00 wt. percent Cr, 0.01 to 0.30 wt. percent Ti, 0.005 to 0.30 wt. percent Zr and 0.0005 to 0.008 wt. percent B as basic elements and further at least one element selected from the group consisting of Sn, Sb and As in the range of 0.03 to 0.5 Wt. percent and the balance being Fe and unavoidable impurities.
  • a high tension tough steel having excellent delayed rupture resisting properties consisting of 0.05 to 0.80
  • wt. percent C 0.05 to 2.00 wt. percent Si, 0.30 to 2.00 wt. percent Mn, 0.05 to 6.00 wt. percent Cr, 0.01 to 0.30 Wt. percent Ti, 0.005 to 0.30 wt. percent Zr and 0.0005 to 0.008 wt. percent B as basic elements, at least one element selected from the group consisting of Sn, Sb and As in the range of 0.03 to 0.50 wt. percent and further at least one element selected from the group consisting of Nb-l-Ta in an amount up to 1.00 wt. percent, W in an amount up to 1.00 wt. percent, Hf in an amount up to 0.50 wt. percent and Pd in an amount up to 1.00 wt. percent, the balance being Fe and unavoidable impurities.
  • a high tension tough steel having excellent resisting properties delayed rupture consisting of 0.05 to 0.80 wt. percent C, 0.05 to 2.00 wt. percent Si, 0.30 to 2.00 wt. percent Mn, 0.05 to 6.00 wt. percent Cr, 0.01 to 0.30 wt. percent Ti, 0.005 to 0.30 wt. percent Zr and 0.0005 to 0.008 wt. percent B as basic elements, at least one element selected from the group consisting of Sn, Sb and As in the range of 0.03 to 0.50 wt. percent and further at least one element selected from the group consisting of M0 in an amount of 0.05 to 1.00 wt. percent Ni in an amount of 0.05 to 5.00 wt. percent, V in an amount of 0.005 to 1.00 wt. percent and Cu in an amount 0.03 to 0.50 Wt. percent, the balance being Fe and unavoidable impurities.
  • a high tension tough steel having excellent delayed rupture resisting properties consisting of 0.05 to 0.80 wt. percent C, 0.05 to 2.00 wt. percent Si, 0.30 to 2.00 wt. percent Mn, 0.05 to 6.00 wt. percent Cr, 0.01 to 0.30 wt. percent Ti, 0.005 to 0.30 wt. percent Zr and 0.0005 to 0.008 wt. percent B as basic elements, at least one element selected from the group consisting of Sn, Sb and As in the range of 0.03 to 0.50 wt. percent, further at least one element selected from the group consisting of Nb+Ta in an amount up to 1.00 wt. percent, W in an amount up to 1.00 wt.
  • Hf in an amount up to 0.50 wt. percent and Pd in an amount up to 1.00 wt. percent, and still further at least one element selected from the group consisting of M0 in an amount of 0.05 to 1.00 Wt. percent, Ni in an amount of 0.05 to 5.00 wt. percent, V in an amount of 0.005 to 1.00 wt. percent and Cu in an amount of 0.03 to 0.50 wt. percent, the balance being Fe and unavoidable impurities.

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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)

Abstract

THIS INVENTION RELATES TO A HIGH TENSION TOUGH STEEL HAVING EXCELLENT PROPERTY RESISTING TO DELAYED RUPTURE, CONSISTING OF 0.05 TO 0.80% C, 0.05 TO 2.00% SI, 0.30 TO 2.00% MN, 0.05 TO 6.00% CR 0.01 TO 0.30% TR, 0.005 TO ELEMENT SELECTED FROM THE GROUP CONSISTING OF SN, SB AND AS, FROM THE GROUP CONSISTING OF NB+TA, W, HF AND PD AND FURTHER FROM THE GROUP CONSISTING OF MO, NI, V AND CU, BALANCE BEING FE AND IMPURITIES.

Description

HIGH TENSION TOUGH STEEL HAVING EXCEL- LENT PROPERTY RESISTING T DELAYED RUPTURE Hisashi Gondo, Isao Kimura, Tuneyasu Watanabe, and Mitsuo Honda, Kitalryushu, Japan, assignors to Yawata Iron & Steel Co., Ltd., Tokyo, Japan No Drawing. Filed Dec. 15, 1967, Ser. No. 690,783
Int. Cl. C22c 39/54 U.S. Cl. 75-126 4 Claims ABSTRACT OF THE DISCLOSURE This invention relates to a high tension tough steel having excellent property resisting to delayed rupture, consisting of 0.05 to 0.80% C, 0.05 to 2.00% Si, 0.30 to 2.00% Mn, 0.05 to 6.00% Cr 0.01 to 0.30% Tr, 0.005 to 0.30% Zr, 0.5 to 0.008% B as basis elements at least one element selected from the group consisting of Sn, Sb and As, from the group consisting of Nb+Ta, W, Hf and Pd and further from the group consisting of Mo, Ni, V and Cu, balance being Fe and impurities This invention relates to a high tension tough steel having an excellent property resisting to delayed rupture and a tensile strength of above 100 kg. mm.
Though in recent years the strength of high tension stels is attaining a higher level than ever, there occur troubles on account of delayed rupture, that is, a phenomenon that a brittle rupture suddently occurs after the lapse of a certain time, while the steel is during the use in the state of given load stress under natural circumstances. This phenomenon is said to be particularly remarkable in the case of a high tension steel having a tensile strength of more than 130 kg./mm. Hydrogen embrittlement, corrosion or static fatigue is said to be the cause of this phenomenon of delayed rupture, and the degree thereof varies with various conditions such as circumstances of application, shape of parts of construction and the presence of heat treatment and the like. However, the cause of delayed rupture should be considered essentially in connection with characteristics of the steel materials.
The object of the present invention is to provide a low alloy high tension steel having strong resistance to delayed rupture and a tensile strength of above 100 kg./ mm. particularly to provide a steel material which can display a delayed rupture resistance far superior to any conventional steel material at such a high level of tensile strength as more than 130-140 kg./mm.
The steel of the present invention has the following chemical composition: that is, it is composed of 0.05 to 0.80 wt. percent C, 0.05 to 2.00 wt. percent Si, 0.30 to 2.00 wt. percent Mn, 0.05 to 6.00 wt. percent Cr, 0.01 to 0.30 Wt percent Ti, 0.005 to 0.30 wt. percent Zr, and 0.0005 to 0.008 wt. percent B as basic alloying elements and further at least one element selected from the group consisting of Sn, Sb and As in an amount of 0.03 to 0.50 wt. percent. However, the object of the present invention can be better achieved, if there is further added to the steel having the above mentioned composition at least one element selected from the group consisting of Nb+Ta, W, Hf and Pd in an amount of less than 1.00 wt. percent in the case of Nb+Ta, less than 1.00 wt. percent in the case of W, less than 0.50 wt. percent in the case of Hf and less than 1.00 wt. percent in the case of Pd. For the purpose of improving mechanical properties and hardenability of the steel of the present invention, however, at least one element selected from the group consisting of Mo, Ni, V and Cu may be added to each of United States Patent Ofice 3,5745% Patented Apr. 13, 1971 the above mentioned two kinds of steels of the present invention respectively in an amount of 0.05 to 1.00 wt. percent Mo, 0.05 to 5.00 wt. percent Ni, 0.005 to 1.00 wt. percent V and 0.03 to 0.50 wt. percent C11.
The steel of the present invention is characterized in that by causing conventional steel materials of various kinds such as Cr steel, Cr-Mo steel, Cr-Mo-Ni steel, Si-Mn steel, Si-Mn-Cr steel and the like, which have been made high tension steels having a tensile strength of more than kg./mm. by heat treatment and/or cold Working, to contain Ti, Zr and B and further at least an element selected from the group consisting of Sn, Sb and As such an excellent property resisting to delayed rupture as can not easily be expected from a sole effect of each element added can be obtained, and still further by adding to the said steel materials having the above mentioned composition at least one element selected from the consisting of Nb+Ta, W, Hf and Pd in the range specified for each element the delayed rupture resisting property obtained by the above mentioned steel materials are all the more improved that such an excellent property resisting to delayed rupture as never attained with any conventional steel material can be obtained.
The reasons why the content of each constituent of the steel of the present invention has been specified as above mentioned shall be explained in the following.
C is added to a steel to impart the strength and hardenability required for the steel, but if the content of C exceeds 0.80 wt. percent, an improvement in the hardenability can no more be expected and there is further danger of the toughness being extremely reduced by the formation of free cementite. Therefore, the upper limit of C was specified as 0.80 wt. percent. On the other hand, if the content of C is too small, the formation of martensite at the time of heat treatment becomes difficult, and a sufficient strength can not be obtained even by subjecting the steel to a cold working. Therefore, the lower limit was specified as 0.05 wt. percent.
Si and Mn are elements necessary for deoxidation in the steel manufacturing process, but moreover effective for improving the hardenability and bettering the strength and toughness. However, if the content of each element is above 2.00 wt. percent, the elfect of bettering the strength and toughness will be weakened and the steel manufacturing operation will be difiicult. Therefore, the upper limit for both elements was made 2.00 wt. percent respectively. On the other hand, as the addition of Si at least in an amount of 0.05 wt. percent is necessary for deoxidation in the steel manufacturing process, the lower limit of Si was specified as 0.05 Wt. percent. The addition of Mn was determined as more than 0.30 wt. percent, because the elfect of Mn of improving the hardenability will be diminished and also the efiect of preventing damage caused by S during a hot working will be weakened, if the content of Mn is too small.
Cr is also added to improving the hardenability, strength and toughness of the steel. However, when the addition exceeds 6.0 wt. percent, the efiiect can not be obtained in proportion to the addition, while no eifect can be obtained, if the addition is below 0.05 wt. percent.
Ti, Zr, B, Sn, Sb and As are very elements, to which the marked improvement in the property resisting to delayed rupture of the steel of the present invention are attributed. By multiplex effects resulted from combining Ti, Zr, B and at least one element selected from the group consisting of Sn, Sb and As in proper amounts such an excellent eifect as can not easily be expected from sole effect of each of these elements can be displayed. How ever, as it was confirmed by the experiments that the addition of each of these elements exceeds a certain limit,
As compared with samples of conventional steel mate rials B1 to B11, among which some samples contain only one of element selected from the group consisting of Ti, Zr and B, but other samples contain none of them, all the samples of the present invention A1 to A18 contain three of elements Ti, Zr and B in addition C, Si and Cr as the basic constituents. However, the reference B1, B2, B7 which contain one of the above mentioned three elements show that by adding only one of these three elements the effect of preventing delayed rupture cannot be obtained.
On the contrary, A1, A2, A3, A13 and A14 of the present invention show that by the addition of at least one element selected from the group consisting of Sn, Sb and As the time up to the occurrence of delayed rupture can be prolonged by a large margin. Also for instance, the comparison of A4 with B4, or A to B5 demonstrates clearly the effect obtained by adding the elements selected from the group of Sn, Sb and As. Further, the samples A6, A7, A8, A11, A14, A15 and A18 show that by adding further at least one element selected from the group consisting of Nb-f-Ta, W, Hf and Pd the property resisting to delayed rupture can be all the more improved, which is particularly distinguished when comparing with the reference samples B4, B5, B6, B7, B9, B and B11 which contain at least one element selected from the group consisting of Mo, Ni, V. In general, Ni, Mo, Cu and V are known as elements which are also efiective for improving the strength, toughness or hardenability of steels. Even when the steel of the present invention contains these elements, however, it does not mean that the object of the present invention might be lost thereby. If these elements are to be added to the steel of the present invention, at least one element selected from this group is preferable to be added in the following ranges: 0.05 to 5.00 wt. percent Ni, 0.05 to 1.00 wt. percent Mo, 0.005 to 1.00 wt. percent V and 0.03 to 0.50 wt. percent Cu. If more than these ranges, the corresponding eifects can not be expected, but less than these, no efiect can be obtained.
On account of an excellent property resisting to delaying rupture owing to its chemical composition as above mentioned, the steel of the present invention is particularly fit for use in the field where the phenomenon of delayed rupture raises a grave technical issue, for instance, for use as high tensile strength bolts, steel wires or bar steels for prestressed concrete or other structure steel materials or parts thereof, in which an extreme high tensile strength is required.
Having thus described the invention, what is claimed is:
1. A high tension tough steel having excellent delayed rupture resisting properties, consisting of 0.05 to 0.80 wt. percent C, 0.05 to 2.00 wt. percent Si, 0.30 to 2.00 wt. percent Mn, 0.05 to 6.00 wt. percent Cr, 0.01 to 0.30 wt. percent Ti, 0.005 to 0.30 wt. percent Zr and 0.0005 to 0.008 wt. percent B as basic elements and further at least one element selected from the group consisting of Sn, Sb and As in the range of 0.03 to 0.5 Wt. percent and the balance being Fe and unavoidable impurities.
2. A high tension tough steel having excellent delayed rupture resisting properties, consisting of 0.05 to 0.80
wt. percent C, 0.05 to 2.00 wt. percent Si, 0.30 to 2.00 wt. percent Mn, 0.05 to 6.00 wt. percent Cr, 0.01 to 0.30 Wt. percent Ti, 0.005 to 0.30 wt. percent Zr and 0.0005 to 0.008 wt. percent B as basic elements, at least one element selected from the group consisting of Sn, Sb and As in the range of 0.03 to 0.50 wt. percent and further at least one element selected from the group consisting of Nb-l-Ta in an amount up to 1.00 wt. percent, W in an amount up to 1.00 wt. percent, Hf in an amount up to 0.50 wt. percent and Pd in an amount up to 1.00 wt. percent, the balance being Fe and unavoidable impurities.
3. A high tension tough steel having excellent resisting properties delayed rupture, consisting of 0.05 to 0.80 wt. percent C, 0.05 to 2.00 wt. percent Si, 0.30 to 2.00 wt. percent Mn, 0.05 to 6.00 wt. percent Cr, 0.01 to 0.30 wt. percent Ti, 0.005 to 0.30 wt. percent Zr and 0.0005 to 0.008 wt. percent B as basic elements, at least one element selected from the group consisting of Sn, Sb and As in the range of 0.03 to 0.50 wt. percent and further at least one element selected from the group consisting of M0 in an amount of 0.05 to 1.00 wt. percent Ni in an amount of 0.05 to 5.00 wt. percent, V in an amount of 0.005 to 1.00 wt. percent and Cu in an amount 0.03 to 0.50 Wt. percent, the balance being Fe and unavoidable impurities.
4. A high tension tough steel having excellent delayed rupture resisting properties, consisting of 0.05 to 0.80 wt. percent C, 0.05 to 2.00 wt. percent Si, 0.30 to 2.00 wt. percent Mn, 0.05 to 6.00 wt. percent Cr, 0.01 to 0.30 wt. percent Ti, 0.005 to 0.30 wt. percent Zr and 0.0005 to 0.008 wt. percent B as basic elements, at least one element selected from the group consisting of Sn, Sb and As in the range of 0.03 to 0.50 wt. percent, further at least one element selected from the group consisting of Nb+Ta in an amount up to 1.00 wt. percent, W in an amount up to 1.00 wt. percent, Hf in an amount up to 0.50 wt. percent and Pd in an amount up to 1.00 wt. percent, and still further at least one element selected from the group consisting of M0 in an amount of 0.05 to 1.00 Wt. percent, Ni in an amount of 0.05 to 5.00 wt. percent, V in an amount of 0.005 to 1.00 wt. percent and Cu in an amount of 0.03 to 0.50 wt. percent, the balance being Fe and unavoidable impurities.
References Cited UNITED STATES PATENTS 1,389,680 9/1921 McKenna -126 1,493,191 5/1924 De Golyer 75126 1,959,398 5/1934 Whitely 75-45 2,867,531 1/ 1959 Holzwarth 75-123 L. DEWAYNE RUTLEDGE, Primary Examiner J. E. LEGRU, Assistant Examiner US Cl. X.R.
75--126D, F, P, N, 128A, C, F, G, Z, T, V, W
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Cited By (18)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3770425A (en) * 1971-07-15 1973-11-06 A Belenky Welding electrode for continuous welding
US3926624A (en) * 1972-03-17 1975-12-16 Jones & Laughlin Steel Corp Production of ferritic stainless steels containing zirconium
US4060431A (en) * 1975-08-23 1977-11-29 Thyssen Edelstahlwerke Aktiengesellschaft Heat-treatable steel
US4127427A (en) * 1975-08-15 1978-11-28 Kobe Steel, Ltd. Super mild steel having excellent workability and non-aging properties
US4129442A (en) * 1976-01-14 1978-12-12 Kawasaki Jukogyo Kabushiki Kaisha Wear- and impact-resisting cast steel
US4171233A (en) * 1978-05-22 1979-10-16 Bethlehem Steel Corporation Lens quality of die steel
US4216014A (en) * 1977-11-22 1980-08-05 Kawasaki Jukogyo Kabushiki Kaisha Low temperature steel alloy
US4318740A (en) * 1979-01-31 1982-03-09 Nippon Gakki Seizo Kabushiki Kaisha Low alloy lead frame
US4319934A (en) * 1979-01-31 1982-03-16 Snap-On Tools Corporation Method of forming tools from alloy steel for severe cold forming
US4322247A (en) * 1979-01-31 1982-03-30 Snap-On Tools Corporation Alloy steel for severe cold forming
US4322256A (en) * 1979-01-31 1982-03-30 Snap-On Tools Corporation Tool made from alloy steel for severe cold forming
US4461657A (en) * 1983-05-19 1984-07-24 Union Carbide Corporation High strength steel and gas storage cylinder manufactured thereof
US4537644A (en) * 1981-09-28 1985-08-27 Nippon Steel Corporation High-tension high-toughness steel having excellent resistance to delayed fracture and method for producing the same
US4578113A (en) * 1983-05-19 1986-03-25 Union Carbide Corporation High strength steel
US5595614A (en) * 1995-01-24 1997-01-21 Caterpillar Inc. Deep hardening boron steel article having improved fracture toughness and wear characteristics
US5928442A (en) * 1997-08-22 1999-07-27 Snap-On Technologies, Inc. Medium/high carbon low alloy steel for warm/cold forming
US20040250931A1 (en) * 2003-01-24 2004-12-16 Ellwood National Forge Company Eglin steel - a low alloy high strength composition
RU2634521C1 (en) * 2017-01-10 2017-10-31 Юлия Алексеевна Щепочкина Ferrous alloy

Cited By (19)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3770425A (en) * 1971-07-15 1973-11-06 A Belenky Welding electrode for continuous welding
US3926624A (en) * 1972-03-17 1975-12-16 Jones & Laughlin Steel Corp Production of ferritic stainless steels containing zirconium
US4127427A (en) * 1975-08-15 1978-11-28 Kobe Steel, Ltd. Super mild steel having excellent workability and non-aging properties
US4060431A (en) * 1975-08-23 1977-11-29 Thyssen Edelstahlwerke Aktiengesellschaft Heat-treatable steel
US4129442A (en) * 1976-01-14 1978-12-12 Kawasaki Jukogyo Kabushiki Kaisha Wear- and impact-resisting cast steel
US4216014A (en) * 1977-11-22 1980-08-05 Kawasaki Jukogyo Kabushiki Kaisha Low temperature steel alloy
US4171233A (en) * 1978-05-22 1979-10-16 Bethlehem Steel Corporation Lens quality of die steel
US4319934A (en) * 1979-01-31 1982-03-16 Snap-On Tools Corporation Method of forming tools from alloy steel for severe cold forming
US4318740A (en) * 1979-01-31 1982-03-09 Nippon Gakki Seizo Kabushiki Kaisha Low alloy lead frame
US4322247A (en) * 1979-01-31 1982-03-30 Snap-On Tools Corporation Alloy steel for severe cold forming
US4322256A (en) * 1979-01-31 1982-03-30 Snap-On Tools Corporation Tool made from alloy steel for severe cold forming
US4537644A (en) * 1981-09-28 1985-08-27 Nippon Steel Corporation High-tension high-toughness steel having excellent resistance to delayed fracture and method for producing the same
US4461657A (en) * 1983-05-19 1984-07-24 Union Carbide Corporation High strength steel and gas storage cylinder manufactured thereof
US4578113A (en) * 1983-05-19 1986-03-25 Union Carbide Corporation High strength steel
US5595614A (en) * 1995-01-24 1997-01-21 Caterpillar Inc. Deep hardening boron steel article having improved fracture toughness and wear characteristics
US5928442A (en) * 1997-08-22 1999-07-27 Snap-On Technologies, Inc. Medium/high carbon low alloy steel for warm/cold forming
US20040250931A1 (en) * 2003-01-24 2004-12-16 Ellwood National Forge Company Eglin steel - a low alloy high strength composition
US7537727B2 (en) * 2003-01-24 2009-05-26 Ellwood National Forge Company Eglin steel—a low alloy high strength composition
RU2634521C1 (en) * 2017-01-10 2017-10-31 Юлия Алексеевна Щепочкина Ferrous alloy

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