US3837846A - Austenitic steel alloy adapted to be welded without cracking - Google Patents

Austenitic steel alloy adapted to be welded without cracking Download PDF

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Publication number
US3837846A
US3837846A US00237488A US23748872A US3837846A US 3837846 A US3837846 A US 3837846A US 00237488 A US00237488 A US 00237488A US 23748872 A US23748872 A US 23748872A US 3837846 A US3837846 A US 3837846A
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percent
weight
manganese
sulfur
titanium
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H Becker
G Kohlert
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Vereinigte Deutsche Metallwerke AG
Ver Deutsche Metallwerke AG
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Ver Deutsche Metallwerke AG
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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

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  • An austenitic steel alloy capable of being welded without cracking by the argon arc-welding process consists of substantially 16 to 35 percent by weight chromium, 15 to 45 percent by weight nickel, 0 to 5 percent by weight molybdenum, 0 to 3 percent by weight copper, 0.1 to 1.5 percent by weight aluminum, 0.01 to 0.10 percent by weight carbon, 0.30 to 0.60 percent by weight silicon, 0 to 0.008 percent by weight calcium, 0 to 0.05 percent by weight zirconium, and manganese, titanium, sulfur and phosphorus in weightpercent concentrations within the area to the left of curve I in the graph of FIG. 2 of the drawing, the balance being iron and the usual (inevitable) impurities.
  • CEACK- FEE'E WELD/IB/L/TV 0.612 1 0.514 7 110 70 la 5 P fi 12001, 0.006- 0.055 abla AUSTENITIC STEEL ALLOY ADAPTED TO BE WELDED WITHOUT CRACKING FIELD OF THE INVENTION
  • Our present invention relates to austenitic steel alloys and, more particularly, to rust-resistant or so-called stainless steels of the nickel-chromium type which are stabilized in the sense that the crystalline configuration or infrastructure is unaffected by welding operations, such as argon arc welding whereby hot cracking does not occur.
  • Austenitic steel alloys of various compositions have been proposed for many purposes and can be welded by argon arc-welding techniques, i.e. filler-free welding under an argon blanket or atmosphere.
  • the compositions of such alloys are adjusted to a deltaferrite concentration of 3 to percent by weight.
  • delta-ferrite in an austenitic matrix is associated with destressing of the crystal structure or infra structure in the hot-cracking range, especially when relatively small cross-sections are welded together without fillers. It has been assumed that the delta-ferrite acts by dissolving substance such as sulfur, phosphorus, arsenic, bismuth, selenium and tellurium which may concentrate during the welding process and give rise to hot cracking. The delta-ferrite, therefore, renders high concentrations of the crack-promoting constituents less detrimental.
  • Another object of the invention is to provide an austenitic-alloy steel having low susceptibility to hot cracking upon argon arc welding without the use of fillers and which is relatively inexpensive or can be produced in an inexpensive manner.
  • FIG. 1 is a graph of the phosphorus and sulfur concentrations plotted in percents by weight along the ordinate, against the nickel concentration plotted in percents by weight along the abscissa, showing the maximum permissible values of phosphorus and sulfur in an austenitic alloy steel which is to be free from cracking in the manner described;
  • FIG. 2 is a composition diagram illustrating the principles of the present invention.
  • FIG. 1 Prior to describing the principles of the present invention in somewhat greater detail, a consideration of FIG. 1 is in order.
  • Known investigations of steels having different concentrations of chromium, nickel sulfur and phosphore have demonstrated that an increased nickel concentration requires a reduction in the phosphorus and sulfur concentrations if weld-cracking is to be avoided.
  • FIG. 1 we have shown in FIG. 1 the maximum permissible concentrations of sulfur and phosphorus plotted in percent by weight along the ordinate, in dependance upon the nickel concentration (plotted in percent by weight along the abscissa), at which weld cracking is excluded.
  • Phosphoric and sulfur concentrations above these levels result in aus tenitic steel alloys susceptible to weld cracking, e.g. when subjected to argon arc welding without filler electrodes.
  • the curves 1, I1 and III define certain zones which can be defined as a zone X corresponding to crack susceptibility underargon arc welding, a zone Y corresponding to a transition range in which crack susceptibility is reduced and a zone Z corresponding to crack-free weldability, Curve 1 represents the boundary to the left of which an improved austenitic steel composition is obtained to the left of the curve, with reduced tendency toward cracking.
  • Curve II represents the boundary of the zone Z, to the left of this boundary being the region in which crack-free welding can be carried out as indicated.
  • the curve 111 represents a linear or pseudolinear approximation of the latter boundary curve and has been provided to facilitate the definition of the manganese and titanium boundary.
  • the sum of the manganese and titanium weight percentages should be related to the sum of the phosphorus and sulfur weight percentages by the relationship (Mn% +Ti%) Z A +B P%) where (3% P%) is defined, for the present purposes, by the value [3 and (Mn% Ti%) is defined as 04.
  • B ranges between 0.0065 to 0.0145 percent, A is preferably 0.05 percent and B 100.
  • B lies above 0.0145 percent, A 9.48 percent and B 750.
  • the silicon concentration may range between 0.3 and 0.6 percent but preferably is 0.5 percent i 0.005 percent.
  • the system contains 0.001 to 0.008 percent by weight calcium, preferably 0.004 to 0.006 percent by weight calcium and/or 0.01 to 0.05 percent by weight zirconium, perferably about 0.02 percent thereof. It has been found to be especially advantageous when the manganese concentration is approximately twice the silicon content.
  • the charges were melted in accordance with known melting processes, for instance, in an electric arc furnacc or induction furnace. Improvement was obtained by a subsequent vacuum treatment but was not essen tial.
  • the charge was preferably teemed under a protective atmosphere.
  • the alloys which can be welded satisfactorily thus lie in the field on the left of the limiting curve.
  • the curve is adjoined on the right by a transitional range, in which welding cracks may be expected. Alloys in which the ratio of the sulfur and phosphorus contents to the manganese and titanium contents is on the right of this range cannot be welded without cracking.
  • FIG. 2 indicates that the formula defines a safe limit, and the alloys may be slightly beyond said limit without a risk of welding cracks. Specifically, no attempt has been made to find a more complicated formula for a better approximation to the limiting curve found in the tests.
  • the linear function which has been selected bet ter defines the relationship between the contents of sulfur and phosphorus, on the one hand, and those of manganese and titanium, on the other hand.
  • the linear substitute function can be used more easily in practice. This formula defining the limiting condition has been selected to facilitate the understanding, however, and is not intended to restrict the scope of the invention.
  • An austenitic steel alloy adapted to be welded without cracking consisting of essentially 16 to 35 percent by weight chromium, 15 to 45 percent by weight nickel, 0 to 5 percent by weight molybdenum, 0 to 3 percent by weight copper, 0.1 to 1.5 percent by weight aluminum, 0.01 to 0.1 percent by weight carbon, 0.30 to 0.60 percent by weight silicon, 0.004 to 0.006 percent by weight calcium, 0 to 0.05 percent by weight zirconium, and an effective amount of manganese, titanium, sulfur and phosphorous limited to the weightpercentage concentrations within the area to the left of the curve I in the graph of FIG. 2 of the drawing, the balance being iron and the usual inevitable impurities.
  • the alloy defined in claim 11 having a silicon content of about 0.02 percent by weight.
  • An austenitic steel alloy adapted to be welded without cracking and consisting of essentially 16 to 35 percent by weight chromium, 15 to 45 percent by weight nickel, 0 to 5 percent by weight molybdenum, 0 to 3 percent by weight copper, 0.1 to 1.5 percent by weight aluminum, 0.01 to 0.1 percent by weight carbon, 0.3 to 0.6 percent by weight silicon, 0.001 to 0.008 percent by weight calcium, 0 to 0.05 percent by weight zirconium, and an effective amount of manganese, titanium, sulfur and phosphorous limited to the weight-percentage concentrations within the area to the left of curve I of the graph of FIG. 2 of the drawing, the balance being iron and theusual inevitable impurities.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Arc Welding In General (AREA)
US00237488A 1971-04-08 1972-03-23 Austenitic steel alloy adapted to be welded without cracking Expired - Lifetime US3837846A (en)

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DE19712117233 DE2117233B2 (de) 1971-04-08 1971-04-08 Verwendung einer stabilaustenitischen stahllegierung fuer die herstellung von nach dem argonare-verfahren ohne zusatzwerkstoffe warmrissfrei verschweissten gegenstaenden

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AT (1) AT327261B (hu)
AU (1) AU466713B2 (hu)
DE (1) DE2117233B2 (hu)
FR (1) FR2135963A5 (hu)
HU (1) HU162963B (hu)
IT (1) IT953617B (hu)
NL (1) NL7203419A (hu)
ZA (1) ZA722219B (hu)

Cited By (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4040876A (en) * 1974-07-02 1977-08-09 Westinghouse Electric Corporation High temperature alloys and members thereof
US4050928A (en) * 1976-02-17 1977-09-27 The International Nickel Company, Inc. Corrosion-resistant matrix-strengthened alloy
US4108641A (en) * 1973-12-22 1978-08-22 Nisshin Steel Company, Limited Oxidation-resisting austenitic stainless steel
US4141762A (en) * 1976-05-15 1979-02-27 Nippon Steel Corporation Two-phase stainless steel
EP0002178A1 (de) * 1977-09-27 1979-06-13 BASF Aktiengesellschaft Verfahren zur Herstellung von Hydroxylammoniumsalzen
US4174213A (en) * 1977-03-04 1979-11-13 Hitachi, Ltd. Highly ductile alloys of iron-nickel-chromium-molybdenum system for gas turbine combustor liner and filler metals
US4431447A (en) * 1982-04-27 1984-02-14 Southwest Research Institute Corrosion resistant weld overlay cladding alloy and weld deposit
US4530720A (en) * 1977-10-12 1985-07-23 Sumitomo Metal Industries, Ltd. High temperature oxidation resistant austenitic steel
WO1989000209A1 (en) * 1987-06-29 1989-01-12 Carondelet Foundry Company Corrosion resistant alloy
US4911886A (en) * 1988-03-17 1990-03-27 Allegheny Ludlum Corporation Austentitic stainless steel
US4959518A (en) * 1989-05-30 1990-09-25 Westinghouse Electric Corp. Method of welding stainless steel studs
US5393487A (en) * 1993-08-17 1995-02-28 J & L Specialty Products Corporation Steel alloy having improved creep strength
US6739333B1 (en) * 1999-05-26 2004-05-25 Boehringer Ingelheim Pharma Kg Stainless steel canister for propellant-driven metering aerosols
US20080078754A1 (en) * 2006-09-28 2008-04-03 Peter Hosemann Method of welding aluminum alloy steels

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS61130464A (ja) * 1984-11-30 1986-06-18 Nippon Steel Corp 高耐食性高強度ドリルカラ−用非磁性鋼

Citations (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2519406A (en) * 1948-07-30 1950-08-22 Westinghouse Electric Corp Wrought alloy
US3184577A (en) * 1963-01-18 1965-05-18 Int Nickel Co Welding material for producing welds with low coefficient of expansion
US3212884A (en) * 1963-07-03 1965-10-19 Marjorie O Soler Ferrous base alloys containing boron
US3300347A (en) * 1964-05-07 1967-01-24 Huck Mfg Co Fastening device and method of making same
US3519419A (en) * 1966-06-21 1970-07-07 Int Nickel Co Superplastic nickel alloys
US3563729A (en) * 1968-04-16 1971-02-16 Crucible Inc Free-machining corrosion-resistant stainless steel
US3573034A (en) * 1967-09-18 1971-03-30 Armco Steel Corp Stress-corrosion resistant stainless steel
US3573899A (en) * 1968-04-17 1971-04-06 Jessop Steel Co Austenitic stainless steel and method
US3594158A (en) * 1966-03-01 1971-07-20 Int Nickel Co Strong,tough,corrosion resistant maraging steel

Patent Citations (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2519406A (en) * 1948-07-30 1950-08-22 Westinghouse Electric Corp Wrought alloy
US3184577A (en) * 1963-01-18 1965-05-18 Int Nickel Co Welding material for producing welds with low coefficient of expansion
US3212884A (en) * 1963-07-03 1965-10-19 Marjorie O Soler Ferrous base alloys containing boron
US3300347A (en) * 1964-05-07 1967-01-24 Huck Mfg Co Fastening device and method of making same
US3594158A (en) * 1966-03-01 1971-07-20 Int Nickel Co Strong,tough,corrosion resistant maraging steel
US3519419A (en) * 1966-06-21 1970-07-07 Int Nickel Co Superplastic nickel alloys
US3573034A (en) * 1967-09-18 1971-03-30 Armco Steel Corp Stress-corrosion resistant stainless steel
US3563729A (en) * 1968-04-16 1971-02-16 Crucible Inc Free-machining corrosion-resistant stainless steel
US3573899A (en) * 1968-04-17 1971-04-06 Jessop Steel Co Austenitic stainless steel and method

Cited By (17)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4108641A (en) * 1973-12-22 1978-08-22 Nisshin Steel Company, Limited Oxidation-resisting austenitic stainless steel
US4040876A (en) * 1974-07-02 1977-08-09 Westinghouse Electric Corporation High temperature alloys and members thereof
US4050928A (en) * 1976-02-17 1977-09-27 The International Nickel Company, Inc. Corrosion-resistant matrix-strengthened alloy
US4141762A (en) * 1976-05-15 1979-02-27 Nippon Steel Corporation Two-phase stainless steel
US4174213A (en) * 1977-03-04 1979-11-13 Hitachi, Ltd. Highly ductile alloys of iron-nickel-chromium-molybdenum system for gas turbine combustor liner and filler metals
EP0002178A1 (de) * 1977-09-27 1979-06-13 BASF Aktiengesellschaft Verfahren zur Herstellung von Hydroxylammoniumsalzen
US4530720A (en) * 1977-10-12 1985-07-23 Sumitomo Metal Industries, Ltd. High temperature oxidation resistant austenitic steel
US4431447A (en) * 1982-04-27 1984-02-14 Southwest Research Institute Corrosion resistant weld overlay cladding alloy and weld deposit
WO1989000209A1 (en) * 1987-06-29 1989-01-12 Carondelet Foundry Company Corrosion resistant alloy
US4824638A (en) * 1987-06-29 1989-04-25 Carondelet Foundry Company Corrosion resistant alloy
US4911886A (en) * 1988-03-17 1990-03-27 Allegheny Ludlum Corporation Austentitic stainless steel
US4959518A (en) * 1989-05-30 1990-09-25 Westinghouse Electric Corp. Method of welding stainless steel studs
US5393487A (en) * 1993-08-17 1995-02-28 J & L Specialty Products Corporation Steel alloy having improved creep strength
US6739333B1 (en) * 1999-05-26 2004-05-25 Boehringer Ingelheim Pharma Kg Stainless steel canister for propellant-driven metering aerosols
US20040211411A1 (en) * 1999-05-26 2004-10-28 Boehringer Ingelheim Pharma Kg Stainless steel canister for propellant-driven metering aerosols
US6983743B2 (en) 1999-05-26 2006-01-10 Boehringer Ingelheim Pharma Kg Stainless steel canister for propellant-driven metering aerosols
US20080078754A1 (en) * 2006-09-28 2008-04-03 Peter Hosemann Method of welding aluminum alloy steels

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DE2117233A1 (de) 1972-10-26
ZA722219B (en) 1973-02-28
NL7203419A (hu) 1972-10-10
HU162963B (hu) 1973-05-28
AU466713B2 (en) 1973-08-23
DE2117233B2 (de) 1973-03-15
AT327261B (de) 1976-01-26
AU3918872A (en) 1973-08-23
FR2135963A5 (hu) 1972-12-22
ATA193972A (de) 1975-04-15
IT953617B (it) 1973-08-10

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