US3902899A - Austenitic castable high temperature alloy - Google Patents

Austenitic castable high temperature alloy Download PDF

Info

Publication number: US3902899A
Authority: US; United States
Prior art keywords: present; amount; alloy; high temperature; austenitic
Prior art date: 1974-05-13
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

US469347A

Other languages

English (en)

Inventor

David L Sponseller

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.)

Cyprus Amax Minerals Co

Original Assignee

Amax 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.)

1974-05-13

Filing date

1974-05-13

Publication date

1975-09-02

1974-05-13 Application filed by Amax Inc filed Critical Amax Inc

1974-05-13 Priority to US469347A priority Critical patent/US3902899A/en

1975-03-14 Priority to CA222,096A priority patent/CA1044924A/en

1975-04-09 Priority to FR7511117A priority patent/FR2271301B1/fr

1975-04-22 Priority to DE19752517780 priority patent/DE2517780A1/de

1975-05-05 Priority to GB1881675A priority patent/GB1474641A/en

1975-09-02 Application granted granted Critical

1975-09-02 Publication of US3902899A publication Critical patent/US3902899A/en

1992-09-02 Anticipated expiration legal-status Critical

Status Expired - Lifetime legal-status Critical Current

Links

229910045601 alloy Inorganic materials 0.000 title claims abstract description 75
239000000956 alloy Substances 0.000 title claims abstract description 75
PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims abstract description 33
229910052759 nickel Inorganic materials 0.000 claims abstract description 17
XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 16
ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 claims abstract description 15
229910052796 boron Inorganic materials 0.000 claims abstract description 15
229910052750 molybdenum Inorganic materials 0.000 claims abstract description 15
239000011733 molybdenum Substances 0.000 claims abstract description 15
ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims abstract description 14
VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims abstract description 13
229910052804 chromium Inorganic materials 0.000 claims abstract description 13
239000011651 chromium Substances 0.000 claims abstract description 13
229910052758 niobium Inorganic materials 0.000 claims abstract description 13
239000010955 niobium Substances 0.000 claims abstract description 13
GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims abstract description 13
OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 12
229910052799 carbon Inorganic materials 0.000 claims abstract description 12
WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 claims abstract description 12
229910052721 tungsten Inorganic materials 0.000 claims abstract description 12
239000010937 tungsten Substances 0.000 claims abstract description 12
229910052710 silicon Inorganic materials 0.000 claims abstract description 11
239000010703 silicon Substances 0.000 claims abstract description 11
PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims abstract description 9
229910052748 manganese Inorganic materials 0.000 claims abstract description 9
239000011572 manganese Substances 0.000 claims abstract description 9
229910052742 iron Inorganic materials 0.000 claims abstract description 8
239000012535 impurity Substances 0.000 claims abstract description 7
238000005260 corrosion Methods 0.000 abstract description 8
230000007797 corrosion Effects 0.000 abstract description 8
230000015572 biosynthetic process Effects 0.000 description 13
235000016768 molybdenum Nutrition 0.000 description 11
239000000470 constituent Substances 0.000 description 9
XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 7
238000005275 alloying Methods 0.000 description 7
230000008901 benefit Effects 0.000 description 6
238000004519 manufacturing process Methods 0.000 description 6
239000000463 material Substances 0.000 description 6
229910000601 superalloy Inorganic materials 0.000 description 6
238000005266 casting Methods 0.000 description 5
238000002844 melting Methods 0.000 description 5
239000000203 mixture Substances 0.000 description 5
238000012360 testing method Methods 0.000 description 4
229910001566 austenite Inorganic materials 0.000 description 3
238000010438 heat treatment Methods 0.000 description 3
230000001965 increasing effect Effects 0.000 description 3
150000001247 metal acetylides Chemical class 0.000 description 3
238000005728 strengthening Methods 0.000 description 3
229910000851 Alloy steel Inorganic materials 0.000 description 2
229910001021 Ferroalloy Inorganic materials 0.000 description 2
230000003466 anti-cipated effect Effects 0.000 description 2
239000003795 chemical substances by application Substances 0.000 description 2
238000002485 combustion reaction Methods 0.000 description 2
230000008018 melting Effects 0.000 description 2
UNASZPQZIFZUSI-UHFFFAOYSA-N methylidyneniobium Chemical compound [Nb]#C UNASZPQZIFZUSI-UHFFFAOYSA-N 0.000 description 2
230000003647 oxidation Effects 0.000 description 2
238000007254 oxidation reaction Methods 0.000 description 2
230000009467 reduction Effects 0.000 description 2
239000006104 solid solution Substances 0.000 description 2
229910000859 α-Fe Inorganic materials 0.000 description 2
RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
229910000583 Nd alloy Inorganic materials 0.000 description 1
OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
206010037660 Pyrexia Diseases 0.000 description 1
NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
230000002411 adverse Effects 0.000 description 1
229910052787 antimony Inorganic materials 0.000 description 1
WATWJIUSRGPENY-UHFFFAOYSA-N antimony atom Chemical compound [Sb] WATWJIUSRGPENY-UHFFFAOYSA-N 0.000 description 1
229910052785 arsenic Inorganic materials 0.000 description 1
RQNWIZPPADIBDY-UHFFFAOYSA-N arsenic atom Chemical compound [As] RQNWIZPPADIBDY-UHFFFAOYSA-N 0.000 description 1
230000008859 change Effects 0.000 description 1
239000010941 cobalt Substances 0.000 description 1
229910017052 cobalt Inorganic materials 0.000 description 1
GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 1
229910052802 copper Inorganic materials 0.000 description 1
239000010949 copper Substances 0.000 description 1
230000001627 detrimental effect Effects 0.000 description 1
239000006185 dispersion Substances 0.000 description 1
230000002708 enhancing effect Effects 0.000 description 1
230000006698 induction Effects 0.000 description 1
239000004615 ingredient Substances 0.000 description 1
WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 1
230000007246 mechanism Effects 0.000 description 1
239000000155 melt Substances 0.000 description 1
238000000034 method Methods 0.000 description 1
230000004048 modification Effects 0.000 description 1
238000012986 modification Methods 0.000 description 1
229910052698 phosphorus Inorganic materials 0.000 description 1
239000011574 phosphorus Substances 0.000 description 1
230000002035 prolonged effect Effects 0.000 description 1
230000009257 reactivity Effects 0.000 description 1
238000009877 rendering Methods 0.000 description 1
238000009628 steelmaking Methods 0.000 description 1
229910052717 sulfur Inorganic materials 0.000 description 1
239000011593 sulfur Substances 0.000 description 1
238000011282 treatment Methods 0.000 description 1

Images

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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
- 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
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
- 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
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese

Definitions

An austenitic castable high temperature alloy having improved high temperature strength coupled with good corrosion resistance and ductility in the as-cast condition and comprising about 16 to about 22% chromium; about 6 to about 18% nickel; about 6 to about 10% molybdenum, up to about 3% tungsten; about 0.5 to-about 2.5% boron; about 0.01 to about 0.4% carbon; about 0.15 to about 7% manganese; up to about 3% silicon; from zero to about 1% niobium; and the balance substantially all iron together with normal residuals and incidental impurities present in usual amounts.
the present invention overcomes many of the problems and disadvantages associated with castable high temperature alloys of similar type heretofore known by providing an iron-base austenitic alloy which can readily be air-melted and. because of very high fluidity. can be cast in accordance with standard foundry practices and wherein the resultant castings are possessed of excellent properties in the as-cast condition. avoiding further costly and time-comsuming heat treating practices of the types heretofore employed.
the comparatively low cost of the present alloy renders it eminently suitable for the manufacture of blades. vanes. and integral wheels for gas turbine engines.
an iron-base austenitic alloy which is comprised of a carefully selected group of alloying constituents employed in controlled amounts to provide a material having unique and balanced properties. cnabling the alloy to be air-melted and cast in accordance with standard foundry practices and wherein the resultant east components are possessed of excellent room temperature and high temperature mechanical properties and corrosion resistance in an as-cast condition. dispensing with the need of costly and time-consuming post-heat treatments.
the alloy is further characterized as one having a stable microstructure which retains the improved properties of the alloy even after prolonged exposure to elevated temperatures during service.
the castable austenitic alloy of the present invention contains about 16% to about 22% chromium. about 6% to about 18%- nickel. and 6% to about 1071 molybdenum. up to about 3% tungsten. 0.5% to about 2.571 boron. about 0.01.71 to about 0.471 carbon. about 0.15% to about 7% manganese. up to about 3% silicon. from zero to about 1% niobium. and the balance substantially all iron together with normal residuals and incidental impurities present in conventional amounts.
the alloy is further characterized as one having a substantially austenitie microstructure in which borides and carbides are present in the interdendritic and intergra n ular boundary phase networks.
the alloy of the present invention can also contain conventional residuals and normal impurities present in the amounts normally encountered in commercial steel-making practices. Such residuals and impurities, when present in normal quantities, do not adversely affect the properties of the alloy which provides for increased flexibility and efficiency in the utilization of scrap iron in accordance with commercial foundry practices.
the chromium constituent as set forth in the table can be employed in amounts ranging from 16 up to about 22%. while quantities in the range of about 17 to 20% are usually preferred.
the chromium constituent contributes oxidation or corrosion resistance to the alloy and also comprises a boride former to produce precipitated chromium boride in the interdendritic and intergranular boundary phase network within the austenitic microstrueture of the alloy. Quantities of chromium less than about 16% result in inadequate corrosion resistance of the alloy, while quantitiesin excess of about 22% result in instability of the microstructure and the formation of undesirable phases during elevated temperature service of components'east of the alloy.
Nickel can be employed in amounts broadly ranging from about 6 up to about 18% and contributes to the formation and stability of the austenitic structure of the alloy. Quantities of nickel less than about 6% result in the formation of an undesirable proportion of ferrite, while quantities in excess of about 18% provide'no appreciable benefits over that obtained by the use of lesser amounts and. therefore, the use of amounts greater than about 18% is undesirable from an economic standpoint.
Molybdenum is employed in an amount ranging from about 6 to about 10%, and preferably from about 7 to about 9%.
the molybdenum constituent contributes strength to the austenitic alloy. both through solidsolution strengthening and by the formation of the intergranular and interdendritic boride and carbide boundary phases. Quantities of molybdenum less than about 6% result in alloys which are generally of inadequate high temperature strength; while quantities in excess of about 10%. depending upon the quantities of other alloying agents present.
tungsten in the alloy is optional and quantities up to about 3% can be employed for enhancing the strength of the alloy by both solid-solution strengthening and the formation of carbide and boride phases in the boundary network. Quantities of tungsten greater than about 3% are undesirable due to the in creased instability of the microstructure and the formation of undesirable phases during service of cast componentsat elevated temperatures. As will be noted in Table l a particularly satisfactory alloy of the enumerated nominal composition need not contain any tungsten in order to achieve the excellent high temperature stress rupture properties coupled with comparatively superior roomternperature ductility.
the boron alloying constituent contributes to the interdendritic and intergranular boride phase strengthening mechanism by the formation of borides containing chromium and molybdenum, as well as tungsten when present.
a fine dispersion of borides within the austenite grains also contributes toward the improved strength properties of the alloy at elevated temperatures.
quantities of boron less than about 0.5% result in an alloy of inadequate strength due to the insufficient formation of the interdendritic and intergranular boride phase network, whereas quantities above about 2.5% generally result in an excessive embrittlement and an undesirable loss of ductility of the as-cast material. It is for this reason that the element boron is controlled within the specific ranges as set forth in Table l.
the presence of carbon contributes to the elevatedtemperature strength of the alloy by the formation of intergranular phases consisting of precipitated carbides of niobium, molybdenum and tungsten, if present.
the carbon also contributes to improved mechanical properties by the formation of finely-dispersed carbide phases, principally niobium carbide, in the austenite.
the carbon content can range from as low as about 0.01 to as high as 0.4%, while quantities of from about 0.05 to about 0.25% are preferred.
the carbon constituent is controlled within the aforementioncd range since quantities in excess of about 0.4% result in excessive brittleness and a loss in the ductility of the alloy.
manganese may broadly range from as low as about 0.15 to as high as about 7%, although quantities of about 0.5 to about 5% are preferred.
the managanese contributes toward the stability of the austenitic structure of the alloy and the specific concentration employed in the alloy can be varied in consideration of the quantity of nickel employed. Normally. quantities of manganese in excess of about 7% are objectionable because of the high degree of reactivity of the molten alloy with the melting vessel, as well as the material of which the casting mold is comprised. When the alloy is cast into molds that have been preheated to high temperatures, such as approximately 18()0F, it is desirable to employ a manganese content of 3% or less.
Silicon comprises an optional constituent in the alloy and generally can be tolerated in amounts up to about 3%, while concentrations of about 0.15%. which corresponds to a normal residual level. up to about 1% are preferred.
Niobium also comprises an optional ingredient. although its presence in concentrations of about 0.2 to about 0.7% is preferred.
the inclusion of niobium in the alloy results in an enhancement of the high temperature strength properties of the alloy as a result of the formation offinely-dispersed niobium carbide phase in the austenite. as well as in the interdendritic and intergranular phase network.
the use of niobium in amounts generally greater than about it: is undesirable due to the resultant reduction in ductility of the alloy.
the balance of the alloy consists essentially-of iron while the nickel yvas added as electrolytic nickel and from that present in ferroalloys. was added as eommercially pure iron.
the melts were deoxidi7ed with alumi along with conventional residuals and incidental impu- 5 num and ⁇ 'er. e poured into test bar specimens using rities present in the usual quantities. A further benefitpreheated lost wax-type molds.
the specific composiof the alloy of the present invention is in its apparent tion of the experimental alloys is set forth in Table 2. toleration of trace quantities of such elements as lead. tin. arsenic. antimony, copper. sulfur. phosphorus. etc... i with any significant detrimental effects on its properl H TABLE 2 ties, 1
tal alloy were subjected to physical and mechanical It will be understo d that th s exa p r ppl testing, including the determination of their respective merely for illustrative purposes and are not intended to w room t m erature-- density, their room temperature be limiting of the scope of the invention as herein de 7 Y 01% offs t i ld Strength (Y5), d l i il scribed and as set forth in the subjoined claims. strength (U l S). their. elevated-temperature ultimate EXAMPLE 1 tensile strength (UTS), as wellas their percent elonga-1 tion at room temperature and elevated temperatures as Three experimental alloys. designated A.
B d 15 an indication of the ductility of the sample alloys.
the respectively. were prepared by air-melting 55-p nd alloys were also subjected to high temp'erature'stressheats in an induction furnace. Th Chr m um. molybrupture tests and the IOU-hour rupture'strength was dedenum. tungsten, niobium, boron, manganese and silitermined. The data obtained are summarized in Table con alloying elements were introduced as ferroalloys; 3.
EXAMPLE 2 An experimental alloy. designated as D, is prepared by air-melting a heat containing the alloying elements asset forth in Table 1 'under the heading Nominal Composition.” From the results obtained on the experimentalvalloys of Example 1. the anticipated properties of alloy- D are a density of 0.287 pounds per cubic inch;
v l Anau'stenitic castable high temperature alloy consisting essentially of about 16 to about 22% chromium, about 6 to about l 87( nickel, about'6 to about 10% molybde num. up to about 371 tungsten, and about 0.5 to about 2.571 boron, about 0.01 to about 0.47rcarbon, about 0. l 5 to about 7% manganese, up to about 3% silicon.
said alloy further characterizedas having a IOO-hour rupture strength at l,500F of at least about 25 ksi;

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Chemical & Material Sciences (AREA)
Engineering & Computer Science (AREA)
Materials Engineering (AREA)
Mechanical Engineering (AREA)
Metallurgy (AREA)
Organic Chemistry (AREA)
Turbine Rotor Nozzle Sealing (AREA)

US469347A 1974-05-13 1974-05-13 Austenitic castable high temperature alloy Expired - Lifetime US3902899A (en)

Priority Applications (5)

Application Number	Priority Date	Filing Date	Title
US469347A US3902899A (en)	1974-05-13	1974-05-13	Austenitic castable high temperature alloy
CA222,096A CA1044924A (en)	1974-05-13	1975-03-14	Austenitic castable high temperature alloy
FR7511117A FR2271301B1 (2)	1974-05-13	1975-04-09
DE19752517780 DE2517780A1 (de)	1974-05-13	1975-04-22	Vergiessbare austenitische hochtemperaturlegierung
GB1881675A GB1474641A (en)	1974-05-13	1975-05-05	Castable austenitic alloy

Applications Claiming Priority (1)

Application Number	Priority Date	Filing Date	Title
US469347A US3902899A (en)	1974-05-13	1974-05-13	Austenitic castable high temperature alloy

Publications (1)

Publication Number	Publication Date
US3902899A true US3902899A (en)	1975-09-02

Family

ID=23863435

Family Applications (1)

Application Number	Title	Priority Date	Filing Date
US469347A Expired - Lifetime US3902899A (en)	1974-05-13	1974-05-13	Austenitic castable high temperature alloy

Country Status (5)

Country	Link
US (1)	US3902899A (2)
CA (1)	CA1044924A (2)
DE (1)	DE2517780A1 (2)
FR (1)	FR2271301B1 (2)
GB (1)	GB1474641A (2)

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number	Priority date	Publication date	Assignee	Title
US4190437A (en) *	1977-12-08	1980-02-26	Special Metals Corporation	Low thermal expansion nickel-iron base alloy
US4294614A (en) *	1979-10-17	1981-10-13	Teledyne Industries, Inc.	Austenitic iron-base cryogenic alloy and arc welding electrode for depositing the same
US4371394A (en) *	1980-11-21	1983-02-01	Carpenter Technology Corporation	Corrosion resistant austenitic alloy
US20160298493A1 (en) *	2015-04-13	2016-10-13	United Technologies Corporation	Cutouts in gas turbine structures for deflection control
CN112143981A (zh) *	2020-09-29	2020-12-29	泰州鑫宇精工股份有限公司	一种高强度耐热钢汽车用铸件制备方法

Citations (4)

* Cited by examiner, † Cited by third party
Publication number	Priority date	Publication date	Assignee	Title
US2432617A (en) *	1945-06-13	1947-12-16	Electro Metallurg Co	Ferrous alloys for high temperature use
US2879194A (en) *	1957-07-12	1959-03-24	Westinghouse Electric Corp	Method of aging iron-base austenitic alloys
US3303023A (en) *	1963-08-26	1967-02-07	Crucible Steel Co America	Use of cold-formable austenitic stainless steel for valves for internal-combustion engines
US3352666A (en) *	1964-11-27	1967-11-14	Xaloy Inc	Precipitation hardening stainless steel alloy

1974
- 1974-05-13 US US469347A patent/US3902899A/en not_active Expired - Lifetime
1975
- 1975-03-14 CA CA222,096A patent/CA1044924A/en not_active Expired
- 1975-04-09 FR FR7511117A patent/FR2271301B1/fr not_active Expired
- 1975-04-22 DE DE19752517780 patent/DE2517780A1/de active Pending
- 1975-05-05 GB GB1881675A patent/GB1474641A/en not_active Expired

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number	Priority date	Publication date	Assignee	Title
US2432617A (en) *	1945-06-13	1947-12-16	Electro Metallurg Co	Ferrous alloys for high temperature use
US2879194A (en) *	1957-07-12	1959-03-24	Westinghouse Electric Corp	Method of aging iron-base austenitic alloys
US3303023A (en) *	1963-08-26	1967-02-07	Crucible Steel Co America	Use of cold-formable austenitic stainless steel for valves for internal-combustion engines
US3352666A (en) *	1964-11-27	1967-11-14	Xaloy Inc	Precipitation hardening stainless steel alloy

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number	Priority date	Publication date	Assignee	Title
US4190437A (en) *	1977-12-08	1980-02-26	Special Metals Corporation	Low thermal expansion nickel-iron base alloy
US4294614A (en) *	1979-10-17	1981-10-13	Teledyne Industries, Inc.	Austenitic iron-base cryogenic alloy and arc welding electrode for depositing the same
US4371394A (en) *	1980-11-21	1983-02-01	Carpenter Technology Corporation	Corrosion resistant austenitic alloy
US20160298493A1 (en) *	2015-04-13	2016-10-13	United Technologies Corporation	Cutouts in gas turbine structures for deflection control
US9771829B2 (en) *	2015-04-13	2017-09-26	United Technologies Corporation	Cutouts in gas turbine structures for deflection control
CN112143981A (zh) *	2020-09-29	2020-12-29	泰州鑫宇精工股份有限公司	一种高强度耐热钢汽车用铸件制备方法

Also Published As

Publication number	Publication date
CA1044924A (en)	1978-12-26
FR2271301A1 (2)	1975-12-12
DE2517780A1 (de)	1975-11-20
GB1474641A (en)	1977-05-25
FR2271301B1 (2)	1978-10-06

Publication	Publication Date	Title
US3165400A (en)	1965-01-12	Castable heat resisting iron alloy
US4437913A (en)	1984-03-20	Cobalt base alloy
US4789412A (en)	1988-12-06	Cobalt-base alloy having high strength and high toughness, production process of the same, and gas turbine nozzle
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US4476091A (en)	1984-10-09	Oxidation-resistant nickel alloy
US5283032A (en)	1994-02-01	Controlled thermal expansion alloy and article made therefrom
CA1044921A (en)	1978-12-26	Nickel base alloys having a low coefficient of thermal expansion
JPH02277740A (ja)	1990-11-14	耐摩耗及び耐食性ニッケルベース合金
US4126495A (en)	1978-11-21	Nickel-base superalloy
US3902899A (en)	1975-09-02	Austenitic castable high temperature alloy
US3118763A (en)	1964-01-21	Cobalt base alloys
US3314784A (en)	1967-04-18	Cobalt-base alloy resistant to thermal shock
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US3793013A (en)	1974-02-19	Cobalt-base tantalum carbide eutectic alloys
JPS6028900B2 (ja)	1985-07-08	デイ−ゼルエンジンのバルブおよびバルブシ−ト用Ｎｉ基合金
US3740212A (en)	1973-06-19	Oxidation resistant austenitic ductile nickel chromium iron
US3497349A (en)	1970-02-24	Air castable nickel alloy valve
US3026199A (en)	1962-03-20	Metal alloy
US3854941A (en)	1974-12-17	High temperature alloy
US2981621A (en)	1961-04-25	High temperature nickel-iron base alloy
US3220829A (en)	1965-11-30	Cast alloy
US3839025A (en)	1974-10-01	High temperature alloy
US4927602A (en)	1990-05-22	Heat and corrosion resistant alloys