US3392065A - Age hardenable nickel-molybdenum ferrous alloys - Google Patents

Age hardenable nickel-molybdenum ferrous alloys Download PDF

Info

Publication number
US3392065A
US3392065A US496657A US49665765A US3392065A US 3392065 A US3392065 A US 3392065A US 496657 A US496657 A US 496657A US 49665765 A US49665765 A US 49665765A US 3392065 A US3392065 A US 3392065A
Authority
US
United States
Prior art keywords
molybdenum
alloys
steels
alloy
strength
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
US496657A
Other languages
English (en)
Inventor
Clarence G Bieber
John R Mihalisin
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.)
Huntington Alloys Corp
Original Assignee
International Nickel Co Inc
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 International Nickel Co Inc filed Critical International Nickel Co Inc
Priority to US496657A priority Critical patent/US3392065A/en
Priority to GB44975/66A priority patent/GB1089690A/en
Priority to ES0332159A priority patent/ES332159A1/es
Priority to AT9548166A priority patent/AT267568B/de
Priority to BE688242D priority patent/BE688242A/xx
Priority to NL6614537A priority patent/NL6614537A/xx
Priority to DE19661533298 priority patent/DE1533298A1/de
Priority to SE13964/66A priority patent/SE337935B/xx
Priority to FR80177A priority patent/FR1500486A/fr
Application granted granted Critical
Publication of US3392065A publication Critical patent/US3392065A/en
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium

Definitions

  • the present invention relates to ferrous alloys and more particularly to ferrous-base alloys which manifest a combination of strength and toughness of such magnitude that the alloys can be used in the fabrication of a host of high strength structural members.
  • toughness As contemplated herein, encompasses more than the standard yardsticks of tensile ductility and reduction in area values. It also includes the ability of a steel to exhibit a high ratio :of notch tensile strength to ultimate tensile strength. Experience has shown that tensile ductility and reduction in area values arrived at from testing smooth (as opposed to notched) specimens are not always an unqualified indicator as to reliability.
  • Notch toughness is a reflection of the ability of a ma- ,terial to yield by plastic flow to localized stress.
  • a crack, notch or other flaw is an initiating point of self-propagationand should a material be sufficiently resistant to the propagation of the flaw, i.e., if it is sufficiently selfyielding," it is considered notch-ductile; if not, it is deemed notch-sensitive or prone tOthe development of deleterious brittle failure characteristics.
  • the propagation of a flaw leading to brittle fracture can be induced by a number of factors, including the heat treatment applied to the material, and is particularly acute in'respect of high strength materials. It is known that as the level of yieldstrength increases the smaller becomes the minimum'size of a flaw which can cause or promote subsequent brittle fracture. Thus, even relativelysmall flaws mustbe taken into consideration. Put another way, in dealing with yield strengths of, say, 100,000 or 150,000 p.s.i., the problem is not nearly as severe as is the case where yield strengthsof 200,000 p.s- .i. and above are involved. The notch-tensile test is well known and is not dwelt upon herein; however, in
  • the steels must manifest a ratio of notch-tensile strength to ultimate tensile strength of at least 1.0 (the notch acuity factor, K, being 10 or greater) to be classed as being notch-ductile.
  • the ratio is at least 1.2.
  • ferrous-base alloys containing special and correlated amounts of certain elements, including nickel, molybdenum, manganese, silicon and carbon, can be provided which afford a highly satisfactory and commercially attractive level of strength and toughness.
  • the present invention contemplates providing ferrous alloys containing 10% to 16% nickel, 6% to 12% molybdenum, the sum of the nickel plus molybdenum being not greater than 27%, up to 1% titanium, up to 1% aluminum, carbon in an amount up to 0.1%, up to 1% cobalt, up to not more than 0.25% manganese, up to not more than 0.25% silicon, and the balance essentially iron.
  • balance or balance essentially when used in referring to the amount of iron in the alloys does not exclude the presence of other elements commonly present as incidental elements, e.g., deoxidizing and cleansing elements, and impurities ordinarily associated therewith in small amounts which do not materially affect the basic characteristics of the alloys.
  • elements such as sulfur, phosphorus, hydrogen, oxygen, nitrogen and the like should be maintained at low levels consistent with corn rnercial practice.
  • supplementary elements may be present in the alloys is follows: up to 2% columbium, e.g., up to 1.5%; up to 4% tantalum, e.g., up to 3%; up to 0.1% boron, e.g., up to 0.05%; up to 0.25% zirconium, e.g., up to 0.15%; up to 2% vanadium, e.g., up to 1.5%; up to 0.1% calcium, e.g., up to 0.075%; up to 1% berryllium, e.g., up to 0.5%; and up to 4% copper, e.g., up to 2%.
  • the respective amounts of the aforementioned supplementary elements be as follows: up to 1% columbium, e.g., 0.1%
  • tantalum e.g., 0.01% to 0.5%
  • Tungsten can be used to replace molybdenum in part on an atom for atom basis, two parts of tungsten by weight for one part of molybdenum, in an amount up to 8% by weight of tungsten.
  • the tungsten not exceed 6% and preferably should not exceed 4%, particularly since molybdenum, in contrast to tungsten, importantly contributes to improved forgeability and/or hot workability and also imparts enhanced ductility characteristics.
  • Chromium can adversely affect the characteristics of the alloys contemplated herein and should preferably be held to impurity levels, i.e., less than 1%. In no event should chromium, if present, exceed In achieving an optimum combination of strength and toughness, the alloys advantageously contain 11% to 15% nickel, 8% to 11% molybdenum, the sum of the nickel plus molybdenum being not greater than 25%, at least one element selected from the group consisting of 0.1% to 1% titanium and 0.1% to 1% aluminum, the sum of the titanium plus aluminum being not greater than 1.5%, up to 0.05% carbon, not more than 0.15% manganese, not more than 0.15% silicon with the balance being substantially iron.
  • steels of the instant invention manifest yield strengths (0.2% offset) from upwards of 150,000 p.s.i. to 300,000 p.s.i. or above, together with tensile elongations of 5% to 20%, reduction in areas of atleast 30%, e.g., 40% to 75%, a high notch-tensile strength, a ratio of notchtensile strength to ultimate tensile strength of at least 1 and preferably of at least 1.2, and are also capable of absorbing substantial levels of impact energy.
  • the element nickel contributes, among other things, to achieving ductility, toughness and a desired martensitic structure upon cooling from hot working or, where used, solution treatment.
  • the subject alloys are austenitic at high temperature and undergo transformation during cooling.
  • excessive amounts of nickel e.g., 19%
  • retained austenite in deleterious amounts can ensue and/or there is danger of excessive austenite reversion upon aging.
  • Austenite reversion can be minimized by using low aging temperatures, e.g., below 700 F., but this, in turn, would significantly impair the strength level of the steels.
  • extremely low nickel contents invite the tendency for formation of ferrite or other undesirable and subversive phases and such phases can wreak havoc with various mechanical characteristics of the steels.
  • Molybdenum confers strengthening and hardening characteristics and, as mentioned above herein, also contributes to good forgeability and ductility. It is preferred that the nickel and molybdenum be correlated such that the sum thereof does not exceed 27% and most advantageously does not exceed about 25% or 26%. This correlation greately contributes to achieving the formation of a satisfactory martensitic condition upon cooling from hot working without the necessity of using additional treatments, such as cold treating. However, it is to be understood that cold treatments as by, for example, refrigeration and/or cold working, are not excluded from the scope of the invention in achieving the desired degree of transformation to martensite.
  • Titanium and/or aluminum serve to provide good deoxidation and malleabilization characteristics. Titanium, for example, serves to fix elements, such as oxygen, nitrogen and carbon.
  • the respective amounts of titanium or aluminum should not exceed about 1%, the total thereof not exceeding 1.5%. While carbon can be present up to 4 0.1%, for optimum results it should not be present in amounts greater than 0.05%, e.g., not more than about 0.03%.
  • the silicon and manganese contents of the steels are of vital'significanceand, in 'accordanceherewith, should be kept to a minimum; otherwise, toughness can be most adversely affected.
  • silicon andrnanganese levels even as low as, say, 0.5% seriously-impair the notch ductility of the steels.
  • the total amount of these elements not exceed 0.30% j and fit is most advantageous to keep each of these elementsat a level of not more than about 0.1%, respectively; however, this is diflicult to consistently achieve commercially because ofpickup of these elements. from rawj-materials, slags, refractories, etc.
  • airor vacuum melting practice can be utilized, preferably followed by consumable electrode melting for optimum effects. It is advantageous to utilize materials of good'purity to there; by minimize theoccurrence of inclusions, contaminants, etc.
  • the initially formed cast ingots should be thoroughly homogenized, as for example, by soaking; at a temperature of about 2200 F. to about 2300 F. for about one hour per inch of cross section. Thereafter, the alloys are hot worked (as by forging, pressing, rolling, etc.) and, if desired, cold worked to desired shape.
  • a plu rality of heating and hot working operations can be used and are advantageous to assure thorough homogenization of the cast structure through diffusion and to break up the cast structure.
  • Hot working can be satisfactorily carried out over a temperature range of 2300 F. or 2200" F. down to 1400 F., e.g., 2150 F. to 1500 F., with suitable finishing temperatures being about 2000 F. down to about 15 00 F.
  • Cooling from hot working is preferably accomplished by air cooling although furnace cooling, quenching, etc., can be employed.
  • the steels can be directly aged (no other processing or heating step being necessary, although solutiontreating or annealing over the range of 1400 F. to 2200 F. can be used if desired) by heating at a temperature of about 750 F. to 1100 F. for about 100 hours to 0.1 hour, the longer aging periods being used in conjunction with the loweraging temperatures. Agingat950 F. to 900 F. for about one to four hours has been found quite satisfactory. With aging times above about an hour or so, temperatures above about 1100 F. should not be used since deleterious austenite reversion can occur. On the other hand, temperatures appreciably below 750 F.
  • the steels can be heated at a temperature as high as 14001 F., e.g., about 1200 F. to 1375" F. and preferably at 1250 F. to 1350 F., for a period of time of notfsreateithan about 30 minutes, e.g., up to 15 minutes, the longer time being associated with. the lower temperature.
  • a period of from a few seconds, e.g., 15 seconds, up to five minutes is satisfactory for the temperaturerange of 12 50 F.to1350F.
  • Alloys Nos. 1, 9 and 11 reflect the highly satisfactory combination of properties characteristic of the invention
  • Alloy K is illustrative of the strikingly adverse-effects of using what might otherwise be considered as small amounts of manganese and silicon. As indicated herein, the respective amounts of these constituents should not exceed 0.25% and it is preferred that the total thereof not exceed 0.3%.
  • alloys contemplated herein are also resistant to stress corrosion cracking.
  • the alloys are useful in the production of such items as bar, rod, plate, castings, wire, etc., and products 'made therefrom, including fasteners, e.g., bolts. Desired shapes are best obtained prior to aging, i.e., in the hot worked or annealed condition since the alloys are comparatively soft and thus are more amenable to shaping operations such as cold working. Further, to minimize processing time, aging temperatures from 850 F. to 950 F. are deemed the TABLE I Ni, Mo, Ti, Al, Hardness, Rockwell "0 percent percent percent percent percent A B O D E F Alloy No.:
  • martensite or substantially martensite include the decomposition and/ or transformation products of austenite obtained upon cooling from the hot working operation (or, where used, a solution annealing treatment). These terms also include transformation products of austenite resulting from the application of a cold treatment, e.g., refrigeration at a temperature down to minus 300 F. and/or cold working.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Treatment Of Steel In Its Molten State (AREA)
US496657A 1965-10-15 1965-10-15 Age hardenable nickel-molybdenum ferrous alloys Expired - Lifetime US3392065A (en)

Priority Applications (9)

Application Number Priority Date Filing Date Title
US496657A US3392065A (en) 1965-10-15 1965-10-15 Age hardenable nickel-molybdenum ferrous alloys
GB44975/66A GB1089690A (en) 1965-10-15 1966-10-07 Steel
ES0332159A ES332159A1 (es) 1965-10-15 1966-10-11 Un procedimiento de fabricacion de acero martensitico.
AT9548166A AT267568B (de) 1965-10-15 1966-10-12 Martensitisch aushärtbarer Stahl
BE688242D BE688242A (enrdf_load_stackoverflow) 1965-10-15 1966-10-14
NL6614537A NL6614537A (enrdf_load_stackoverflow) 1965-10-15 1966-10-14
DE19661533298 DE1533298A1 (de) 1965-10-15 1966-10-14 Martensitaushaertbare Nickel-Molybdaen-Stahl-Legierung
SE13964/66A SE337935B (enrdf_load_stackoverflow) 1965-10-15 1966-10-14
FR80177A FR1500486A (fr) 1965-10-15 1966-10-15 Acier susceptible d'un revenu à l'état martensitique

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
US496657A US3392065A (en) 1965-10-15 1965-10-15 Age hardenable nickel-molybdenum ferrous alloys

Publications (1)

Publication Number Publication Date
US3392065A true US3392065A (en) 1968-07-09

Family

ID=23973588

Family Applications (1)

Application Number Title Priority Date Filing Date
US496657A Expired - Lifetime US3392065A (en) 1965-10-15 1965-10-15 Age hardenable nickel-molybdenum ferrous alloys

Country Status (9)

Country Link
US (1) US3392065A (enrdf_load_stackoverflow)
AT (1) AT267568B (enrdf_load_stackoverflow)
BE (1) BE688242A (enrdf_load_stackoverflow)
DE (1) DE1533298A1 (enrdf_load_stackoverflow)
ES (1) ES332159A1 (enrdf_load_stackoverflow)
FR (1) FR1500486A (enrdf_load_stackoverflow)
GB (1) GB1089690A (enrdf_load_stackoverflow)
NL (1) NL6614537A (enrdf_load_stackoverflow)
SE (1) SE337935B (enrdf_load_stackoverflow)

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4443254A (en) * 1980-10-31 1984-04-17 Inco Research & Development Center, Inc. Cobalt free maraging steel
US4579590A (en) * 1983-03-16 1986-04-01 Mitsubishi Jukogyo Kabushiki Kaisha High strength cobalt-free maraging steel
US4832909A (en) * 1986-12-22 1989-05-23 Carpenter Technology Corporation Low cobalt-containing maraging steel with improved toughness
US4871511A (en) * 1988-02-01 1989-10-03 Inco Alloys International, Inc. Maraging steel
FR2774396A1 (fr) * 1998-02-04 1999-08-06 Imphy Sa Acier maraging sans cobalt et sans titane
EP4450186A1 (en) * 2023-04-19 2024-10-23 Sandvik Machining Solutions AB Managing steel powder free from co, ti, and al

Families Citing this family (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4340435A (en) * 1980-10-17 1982-07-20 Bell Telephone Laboratories, Incorporated Isotropic and nearly isotropic permanent magnet alloys
AT374846B (de) * 1982-09-15 1984-06-12 Voest Alpine Ag Herzstueck, insbesondere herzstueckspitze, fuer schienenkreuzungen oder -weichen, sowie verfahren zu seiner herstellung
FR2774099B1 (fr) * 1998-01-23 2000-02-25 Imphy Sa Acier maraging sans cobalt

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3093519A (en) * 1961-01-03 1963-06-11 Int Nickel Co Age-hardenable, martensitic iron-base alloys
US3123506A (en) * 1964-03-03 Alloy steel and method
US3262777A (en) * 1964-07-13 1966-07-26 Int Nickel Co Ultra tough maraging steel

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3123506A (en) * 1964-03-03 Alloy steel and method
US3093519A (en) * 1961-01-03 1963-06-11 Int Nickel Co Age-hardenable, martensitic iron-base alloys
US3262777A (en) * 1964-07-13 1966-07-26 Int Nickel Co Ultra tough maraging steel

Cited By (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4443254A (en) * 1980-10-31 1984-04-17 Inco Research & Development Center, Inc. Cobalt free maraging steel
US4579590A (en) * 1983-03-16 1986-04-01 Mitsubishi Jukogyo Kabushiki Kaisha High strength cobalt-free maraging steel
US4832909A (en) * 1986-12-22 1989-05-23 Carpenter Technology Corporation Low cobalt-containing maraging steel with improved toughness
US4871511A (en) * 1988-02-01 1989-10-03 Inco Alloys International, Inc. Maraging steel
FR2774396A1 (fr) * 1998-02-04 1999-08-06 Imphy Sa Acier maraging sans cobalt et sans titane
EP0935007A1 (fr) * 1998-02-04 1999-08-11 Imphy S.A. Acier maraging sans cobalt et sans titane
US6136102A (en) * 1998-02-04 2000-10-24 Imphy Ugine Pricision Maraging steel
EP4450186A1 (en) * 2023-04-19 2024-10-23 Sandvik Machining Solutions AB Managing steel powder free from co, ti, and al
WO2024217920A1 (en) * 2023-04-19 2024-10-24 Sandvik Machining Solutions Ab Maraging steel powder free from co, ti, and al

Also Published As

Publication number Publication date
FR1500486A (fr) 1967-11-03
BE688242A (enrdf_load_stackoverflow) 1967-04-14
GB1089690A (en) 1967-11-01
DE1533298A1 (de) 1970-03-05
SE337935B (enrdf_load_stackoverflow) 1971-08-23
NL6614537A (enrdf_load_stackoverflow) 1967-04-17
AT267568B (de) 1969-01-10
ES332159A1 (es) 1967-11-01

Similar Documents

Publication Publication Date Title
US5424028A (en) Case carburized stainless steel alloy for high temperature applications
US3093519A (en) Age-hardenable, martensitic iron-base alloys
JP2023515115A (ja) 採掘チェーン用鋼およびその製造方法
US8192560B2 (en) Hardened martensitic steel, method for producing a component from this steel and component obtained in this manner
EP1003922B1 (en) High-strength, notch-ductile precipitation-hardening stainless steel alloy
EP0859869B1 (en) High-strength, notch-ductile precipitation-hardening stainless steel alloy
WO2007016004A1 (en) Corrosion-resistant, cold-formable, machinable, high strength, martensitic stainless steel
USRE28523E (en) High strength alloy steel compositions and process of producing high strength steel including hot-cold working
US3359094A (en) Ferrous alloys of exceptionally high strength
US3132937A (en) Cast steel
US5238645A (en) Iron-aluminum alloys having high room-temperature and method for making same
US3392065A (en) Age hardenable nickel-molybdenum ferrous alloys
JP2019077911A (ja) 鋼部材および鋼部材の製造方法
US3093518A (en) Nickel alloy
US4798634A (en) Corrosion resistant wrought stainless steel alloys having intermediate strength and good machinability
US3262777A (en) Ultra tough maraging steel
CN109790602B (zh) 钢
US3355280A (en) High strength, martensitic stainless steel
US3342590A (en) Precipitation hardenable stainless steel
US3347663A (en) Precipitation hardenable stainless steel
US3318690A (en) Age hardening manganese-containing maraging steel
US3294527A (en) Age hardening silicon-containing maraging steel
JPH04231438A (ja) 析出硬化性工具鋼
US3132938A (en) Aged steel
US4049430A (en) Precipitation hardenable stainless steel