US3663312A - Nitride-strengthened, stainless steel - Google Patents

Nitride-strengthened, stainless steel Download PDF

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US3663312A
US3663312A US17487A US3663312DA US3663312A US 3663312 A US3663312 A US 3663312A US 17487 A US17487 A US 17487A US 3663312D A US3663312D A US 3663312DA US 3663312 A US3663312 A US 3663312A
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nitride
temperature
dispersoid
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microns
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Lynn E Kindlimann
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Allegheny Ludlum Corp
Pittsburgh National Bank
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Allegheny Ludlum Steel 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium

Definitions

  • An article comprising at least one layer which consists essentially of a nitride-strengthened, austenitic stainless steel.
  • the steel contains as a dispersoid therein particles of metal nitride having a free energy of formation of greater than 2l,000 cal./mole, present at an interparticle spacing of less than about 10 microns and has a microstructure comprised of elongated primary grains which contain twins and sub-grains; wherein a substantial number of said primary grains are greater than 20 microns wide and substantially longer than 40 microns.
  • It comprises the steps of: providing a nitride-strengthened, austenitic stainless steel which contains as a dispersoid therein particles of metal nitride having a free energy of formation of greater than 2l,000 caL/mole, present at an interparn'cle spacing of less than about 10 microns; warm working the steel at a temperature below its recrystallization temperature; and annealing the steel at a temperature at or in excess of its germination temperature.
  • the present invention relates to a nitride-strengthened, austenitic stainless steel and more particularly to a nitridestrengthened, austenitic stainless steel with improved high temperature properties. It further related to a method for producing a nitride-strengthened, austenitic stainless steel and more particularly to a method for producing a nitridestrengthened, austenitic stainless steel with improved high temperature properties.
  • a material which can fill the need is a nitridestrengthened, stainless steel which contains as a dispersoid therein particles of metal nitride, having a free energy of formation of greater; i.e., more negative, than -2l,000 cal. lmole at room temperature, present at an interparticle spacing of less than about microns; e.g., less than about 2 microns, and preferably less than 1 micron; e.g., less than about 0.5 micron.
  • the metal nitride can be of a metal such as titanium, aluminum, vanadium or columbium, and is preferably titanium.
  • austenitic stainless steels can be materially improved if the steels are treated to develop a particular stable and creep-resistant microstructure.
  • This particular microstructure is comprised of elongated primary grains which contain twins and sub-grains and is further characterized in that a substantial number of the primary grains are greater than microns wide and substantially longer than 40 microns.
  • the number of such primary grains in excess of 20 microns wide and 40 microns long should be sufficient to improve the properties of the steel; i.e., they should be sufficient to at least double the rupture life of the untreated steel at low stress levels; e.g., 5 ksi, at high temperatures; e. g, 2000F.
  • FIG. 1 is a photomicrograph at 250X of a nitridestrengthened, austenitic stainless steel in the asextruded condition;
  • FIG. 2 is a photomicrograph at 250x of a nitridestrengthened, austenitic stainless steel which has been warm swaged and annealed subsequent to extrusion;
  • FIG. 3 is a photomicrograph at 250x of a nitridestrengthened, austenitic stainless steel which has been cold swaged and annealed subsequent to extrusion;
  • FIG. 4 is a photomicrograph at 250X of a nitridestrengthened, austenitic stainless steel and which has been annealed subsequent to extrusion;
  • FIG. 5 is a photomicrograph at 250X of a nitridestrengthened, austenitic stainless steel which has been warm swaged subsequent to extrusion.
  • the article of the present invention is comprised of at least one layer which consists essentially of nitride-strengthened, austenitic stainless steel having high temperature properties; e.g., high temperature rupture strength characteristics, which are superior to previously known and described nitridestrengthened, stainless steel and which are attributed to the steels particular texturized microstructure which minimizes the generation of dislocations.
  • nitride-strengthened stainless steels it contains as a dispersoid therein, particles of metal nitride, having a free energy of formation of greater than 2l,000 cal.
  • the metal nitride can be of a metal such as titanium, aluminum, vanadium or columbium, and is preferably titanium.
  • the particular microstructure which belongs to the nitridestrengthened, stainless steel layer of this invention is comprised of elongated primary grains which contain twins; i.e., regions in which the crystal lattice has been rotated into an orientation that is related to the orientation of the untwinned lattice in a definite symmetrical manner, and sub-grains and is further characterized in that a substantial number of the primary grains are greater than 20 microns wide and substantially longer than 40 microns.
  • twins i.e., regions in which the crystal lattice has been rotated into an orientation that is related to the orientation of the untwinned lattice in a definite symmetrical manner, and sub-grains and is further characterized in that a substantial number of the primary grains are greater than 20 microns wide and substantially longer than 40 microns.
  • the described structure should comprise at least 50 percent of the steels microstructure but it can comprise at little as 20 percent.
  • the article of this invention can be comprised of one or more layers of nitride-strengthened, austenitic stainless steel; e.g., a number of layers of nitride-strengthened, austenitic stainless steel can be pressure bonded together as described in U.S. Pat. application Ser. No. 803,442, filed on Feb. 28, 1969.
  • the article can comprise at least one layer of nitride-strengthened, austenitic stainless steel and one or more dissimilar layers such as a precipitation hardening alloy; e.g., 54% Ni, 19% Cr, 11% Co, 10% Mo, 3% Ti, 1.5% Al and residuals, or a corrosion resistant alloy; e.g., 47% Ni, 22% Cr, 20% Fe, 9% Mo and residuals.
  • a precipitation hardening alloy e.g., 54% Ni, 19% Cr, 11% Co, 10% Mo, 3% Ti, 1.5% Al and residuals
  • a corrosion resistant alloy e.g., 47% Ni, 22% Cr, 20% Fe, 9% Mo and residuals.
  • each layer of nitride-strengthened, austenitic stainless steel has a rupture strength of no less than 4 ksi for 200 hours at 2,000F when in sheet form.
  • the method of this invention produces a nitridestrengthened, austenitic stainless steel having the particular microstructure described above; i.e., a microstructure comprised of elongated primary grains containing twins and subgrains which is further characterized in that a substantial number of the primary grains are greater than 20 microns wide and substantially longer than 40 microns. It comprises the steps of: providing a nitride-strengthened, austenitic stainless steel which contains as a dispersoid therein particles of metal nitride, having a free energy of formation of greater than 2l,000 cal.
  • nitride contained within the steel can be of metal such as titanium, aluminum, vanadium or columbium, and is preferably titanium.
  • Warm working should be performed at a temperature below the recrystallization temperature of the steel being treated; i.e., the temperature at which equiaxed fine grains are formed. Material which is warm worked at a temperature of or in excess of the recrystallization temperature will not store up enough energy to insure germination during the subsequent high temperature anneal and will not form the elongated grains which are necessary if the heat treatment is to yield the desired microstructure subsequent to annealing.
  • the exact recrystallization temperature cannot, however, be stated as it changes with variables such as the particular composition of the steel and the interparticle spacing of the metal nitride particles.
  • a maximum warm working temperature of 2100F is generally employed to insure maintaining a fibrous unrecrystallized grain structure during heavy warm working reductions (heavy reductions increase the likelihood of recrystallization occuring).
  • a maximum warm working temperature of 1600F is, however, believed to be beneficial.
  • Material which is warm worked at higher temperatures requires a greater reduction to cause formation of the desired structure after annealing than does material warm worked at lower temperatures; e.g., a material warm worked at l300F might require a 30 percent reduction whereas the same material warm worked at l700F might require a 45 percent reduction.
  • the minimum warm working temperature is dependent upon attaining a degree of plasticity which enables the steel to be worked without causing nitride particles to break loose from the matrix. lt, like the recrystallization temperature, cannot be precisely set forth as it depends upon variables such as the thickness of the steel as well as the particular composition of the steel and the interparticle spacing of the metal nitride particles. As a general rule it is in excess of 800F. A minimum warm working temperature of 1200F is, however, preferred as it reduces the depth of edge checking.
  • the degree of warm working is dependent upon many variables which include the composition of the steel, its grain size and the interparticle spacing of the metal nitride particles. As a practical matter it is generally in excess of that required to reduce the cross-sectional area of the steel by 5 percent.
  • High temperature annealing is the part of the process during which the steel obtains the desired microstructure.
  • a rapid; e.g., 5 to 60 minutes, treatment should be performed at a temperature at or in excess of the germination temperature; i.e., the temperature at which abnormal grain growth begins.
  • the germination temperature cannot be precisely set forth as it changes with variables such as the particular composition of the steel and the interparticle spacing of the metal nitride particles.
  • a minimum of 2300F is often employed as the germination temperatures of nitride-strengthened, austenitic stainless steels are generally in excess of 2300F.
  • Germination temperatures below 2300F are, however, characteristic of those steels with larger interparticle spacings. Steels which possess the very desirable small interparticle spacings are generally annealed at a temperature in excess of 2400F.
  • a number of nitride-strengthened, austenitic stainless steel samples were prepared for testing from powder containing by weight approximately 0.026% C, 0.29% Mn, 0.49% Si, 18.33% Cr, 13.50% Ni, 1.95% Ti, balance iron and incidental impurities and by volume 3.85% titanium nitride.
  • the samples were prepared by heating the powder to 2,000F and extruding it to a round bar in a carbon steel can at an extrusion ratio of 23: l
  • the samples were then broken up into five groups; groups A, B, C, D and E.
  • the group A sample was set aside without any further treatment.
  • Group B samples were warm swaged 40-45 percent starting at a temperature of l900F and finishing at a temperature of l300F with intermittent reheating and subsequently annealed for one hour at 2480F in air.
  • Group C samples were cold swaged 4045 percent and subsequently annealed for one hour at 2480F in air.
  • Group D samples were annealed for one hour at 2480F in air.
  • Group E samples were warm swaged 40-45 percent starting at a temperature of 1900F and finishing at a temperature of 1300F with intermittent reheating.
  • microstructure of the groups A, B, C, D and E samples were studies and respectively recorded in FIGS. 1-5. These microstructures were taken from longitudinal sections; i.e., parallel to the major axis of the bar.
  • sample B which was tested at 5 ksi did not fail after 900 hours whereas sample A failed after 62.3 hours, sample C, failed after 35.9 hours, sample D failed after 45.2 hours and sample E, failed after 97.6 hours at 5 ksi. Furthermore, sample B, which was tested at 6 ksi did not fail until 202 hours passed, whereas sample C, which was tested at 6 ksi failed after 7.1 hours.
  • FIG. 2 which is the photomicrograph of the warm swaged and annealed samples; i.e., samples B, and B is comprised of elongated primary grains which contain twins and sub-grains and is further characterized in that a substantial number of the primary grains are greater than 20 microns wide and substantially longer than 40 microns. To the contrary; FIG.
  • FIG. 1 which is the photomicrograph of the as-extruded sample; i.e., sample A, is comprised of fibrous grains which are approximately 2 to 20 microns wide and 300-1000 microns long;
  • FIG. 3 which is the photornicrograph of the cold swaged and annealed samples; i.e., samples C,, C, and C is comprised of mostly equiaxed small grains;
  • FIG. 4 which is the photomicrograph of the annealed sample; i.e., sample D, is comprised of very fine grains; and FIG.
  • samples E, and E which is the photomicrograph of the warm swaged samples; i.e., samples E, and E is comprised of very thin; e.g., less than 10 microns, elongated grains having a length of width ratio considerably higher than the as-extruded sample; i.e., sample A.
  • An article comprising at least one layer which consists essentially of a nitride-strengthened, austenitic stainless steel containing as a dispersoid therein particles of metal nitride present at an interparticle spacing of less than about 10 microns and having a free energy of formation of greater than -2l,000 cal. lmole at room temperature; said nitridestrengthened austenitic stainless steel having a microstructure comprised of elongated primary grains which contain twins and sub-grains, a substantial number of said primary grains being greater than 20 microns wide and substantially longer than 40 microns.
  • said dispersoid is a nitride of a metal from the group consisting of titanium, aluminum, vanadium and columbium.
  • dispersoid is a nitride of metal from the group consisting of titanium, aluminum, vanadium and columbium and wherein said dispersoid particles are present at an interparticle spacing of less than about 0.5 micron.
  • said dispersoid is titanium nitride wherein said titanium nitride particles are present at an interparticle spacing of less than about 2 microns.
  • dispersoid is a nitride of a metal from the group consisting of titanium, aluminum, vanadium and columbium and wherein said dispersoid particles are present at an interparticles spacing of less than about 1.0 micron.
  • An article according to claim 1 including at least one layer which is dissimilar to nitride-strengthened, austenitic stainless steel.
  • each layer of nitride-strengthened, austenitic stainless steel has a rupture strength of no less than about 4 ksi for 200 hours at 2000F.
  • a method of improving the high temperature properties of nitride-strengthened, austenitic stainless steel which comprises the steps of'. providing a nitride-strengthened, austenitic stainless steel containing as a dispersoid therein particles of metal nitride present at an interparticle spacing of less than about 10 microns and having a free energy of formation of grater than 21,000 cal. lmole at room temperature; warm working said steel at a temperature below its recrystallization temperature; and annealing said steel at a temperature at least equal to its germination temperature.
  • a method according to claim 13 wherein said warm working is at a temperature of from about 800F to about 2,100F.
  • a method according to claim 13 wherein said annealing is at a temperature of at least about 2,300F.
  • said dispersoid is a nitride of a metal from the group consisting of titanium, aluminum, vanadium, and columbium.
  • a method according to claim 19 wherein said warm working is at a temperature of from about 800F to about 1600F.
  • a method according to claim 22 wherein said annealing is at a temperature of at least about 2400F.
  • a method according to claim 13 wherein said dispersoid is titanium nitride and wherein said titanium nitride particles are present at an interparticle spacing of less than about 1 micron.

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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)
  • Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
US17487A 1970-03-09 1970-03-09 Nitride-strengthened, stainless steel Expired - Lifetime US3663312A (en)

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CA (1) CA932986A (enrdf_load_stackoverflow)
DE (1) DE2111245A1 (enrdf_load_stackoverflow)
FR (1) FR2084382A5 (enrdf_load_stackoverflow)
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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3778235A (en) * 1969-02-28 1973-12-11 Allegheny Ludlum Ind Inc Nitride-strengthened stainless steel composite
US4422884A (en) * 1977-10-20 1983-12-27 Concast Ag Method of treating a continuously cast strand formed of stainless steel

Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2703298A (en) * 1949-10-14 1955-03-01 Robertshaw Fulton Controls Co Process for annealing stainless steel

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB398834A (en) * 1931-03-14 1933-09-14 Commentry Fourchambault Et Dec Improvements in and relating to the nitrogenisation of ferrous austenitic alloys
AT284787B (de) * 1964-06-01 1970-09-25 Du Pont Verfahren zur Herstellung von Metallnitriden
GB1146712A (en) * 1965-06-02 1969-03-26 Mannesmann Ag Improved method of producing nitrogen-containing chromium-steel alloys
SE362445B (enrdf_load_stackoverflow) * 1968-06-07 1973-12-10 Allegheny Ludlum Steel
US3672037A (en) * 1969-02-28 1972-06-27 Allegheny Ludlum Steel Nitride strengthened stainless steel composite and production thereof

Patent Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2703298A (en) * 1949-10-14 1955-03-01 Robertshaw Fulton Controls Co Process for annealing stainless steel

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
Dissertation Abstracts, Aug. 1966, Vol. 27, No. 2, 501 B Chen, Dispersion Strengthening of Iron Alloys by Internal Nitriding *

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3778235A (en) * 1969-02-28 1973-12-11 Allegheny Ludlum Ind Inc Nitride-strengthened stainless steel composite
US4422884A (en) * 1977-10-20 1983-12-27 Concast Ag Method of treating a continuously cast strand formed of stainless steel

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SE403136B (sv) 1978-07-31
CA932986A (en) 1973-09-04
DE2111245A1 (de) 1971-09-23
FR2084382A5 (enrdf_load_stackoverflow) 1971-12-17

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