EP0366655B1 - Bestandteile oxidationsbeständiger eisenlegierungen - Google Patents
Bestandteile oxidationsbeständiger eisenlegierungen Download PDFInfo
- Publication number
- EP0366655B1 EP0366655B1 EP88903643A EP88903643A EP0366655B1 EP 0366655 B1 EP0366655 B1 EP 0366655B1 EP 88903643 A EP88903643 A EP 88903643A EP 88903643 A EP88903643 A EP 88903643A EP 0366655 B1 EP0366655 B1 EP 0366655B1
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- EP
- European Patent Office
- Prior art keywords
- alloy
- weight
- alloys
- elements
- nickel
- 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
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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
Definitions
- This invention relates to iron-base alloy compositions.
- the compositions relate to nickel containing austenitic ferrous alloy compositions, especially low nickel compositions.
- this invention relates to dopants added to low nickel austenitic alloys as a means of improving the elevated temperature oxidation resistance. This invention may be extended to apply to cast alloys.
- sheet metal automotive exhaust system parts would offer the advantages of both lighter weight and reduced thermal mass.
- the metal thickness of wrought automotive engine parts such as thermal reactors and turbocharger housings, should be minimized. This can be accomplished by constructing the engine parts from stainless steels, austenitic where hot strength is required, and with alloying suitable for resistance to deterioration by engine exhaust gases on the inside surface of the engine parts and atmospheric air on the outside surface of the engine parts where the surface operating temperature is at a maximum.
- Such a construction is not cost effective because the resistance to oxidation of the lower cost stainless steel sheet metal alloys at elevated temperatures of 815.6°C to 1204.4°C (1,500 degrees F to 2,200 degrees F)is not sufficient to allow their use in applications where the alloy is exposed to the combustion products normally formed by gasoline fueled internal combustion engines. Because the presently available low-cost alloys do not resist oxidation in elevated temperature combustion environments, it is necessary to use a more expensive alloy with a higher nickel and/or chromium content in automotive emission control devices such as thermal reactors. Therefore, the limitation to using currently available, adequate alloy content stainless steels is the high cost and excessive strategic element content.
- Degradation of alloy materials, such as stainless steels, at elevated temperatures is largely dependent on the protective capacity of surface oxide films formed from the alloy during exposure to heat in oxygen containing atmospheres.
- the SU-A-553 304 teaches an iron-base alloy composition containing Ca, Mg and Y wherein the amounts of Ca and Mg are in the ranges of 0.001-0.08 and 0.001-0.05 % by weight, respectively. Y added as a dopant element is used in amounts of 0.001-0.1 % by weight.
- the object of the invention is to provide an iron-base alloy composition which has especially good and significant and reproducible characteristics with regard to one or more oxidation resistant properties of the final composition.
- compositions of the present invention relate to the discovery that certain elements can be added to iron-base alloy materials to dramatically improve their resistance to oxidation. More particularly, the invention relates to the discovery that the addition of these elements (referred to herein as "dopants") yields lower cost materials suitable for use in heretofore impractical environments.
- the compositions of the present invention comprise iron-base alloy compositions exhibiting improved resistance to oxidation comprising the components according to patent claim 1.
- alloy materials such as low nickel austenitic (LNA) stainless steel alloys containing chromium and ferritic stainless steel alloys containing medium to high levels of chromium with the additions of the dopants or doping elements or alloys disclosed herein.
- Alloy compositions of the present invention would be made in a conventional manner, i.e., typical of the alloy content without the dopant of the present invention, but with provision for the addition of dopant elements, in the melt process or later, in later alloy processing, or by surface treatment.
- compositions disclosed herein contain small quantities of elements (appearing for the most part in Groups LA, ILA, and IIB of the Periodic Table of Elements) to the base alloy composition. These elements, as ions, enter into the protective oxide scale and modify predominantly anion and to a lesser extent cation transport through the oxide scale, greatly reducing the amount of oxidation observed due to elevated temperature exposure.
- Austenite Stabilizers Alloys of this invention are designed to maintain a stable austenitic matrix at use temperatures up to 1204°C (2200 degrees F). Elements identified as promoting this austenite stability are Mn, Co, Ni, Cu, C, Sn, Sb, Bi and N. Throughout the course of this alloy development, it was necessary to periodically adjust the choice and quantity of austenite stabilizer elements to balance the counteracting effects of La-Ce, Ti, Zr, V, Cr, Al and Si as these elements were introduced or changed in concentration as part of the effort to determine their effect on oxidation resistance.
- An object of this invention is to improve the protective nature of surface oxides formed during exposure to elevated temperatures and, therefore, a stable surface oxide is required.
- Elements identified as significant contributors to stable surface oxide formation on these iron base alloys are: Cr, Co, Ni, Al and Si.
- the elements Cr, Co and Ni were, individually or in combination, part of the base composition, Table II, and therefore not subject to evaluation during the fractional factorial phase of this investigation.
- Al and Si were incorporated into the initial experimental design (Table I) and were determined to contribute to improved oxidation resistance through interaction with dopant elements. This interaction is interpreted to be due to the contribution of Al and Si in formation of stable surface oxides.
- Dopants are elements found to have a major effect on the protective nature of the host oxide. Typically, they are found in groups IA, IIA and IIIB of the Periodic Table of Elements and include, without limitation, those described herein, as well as mixtures of these materials. Their function in improving oxidation resistance is judged to be due to their effect on predominantly anion and to a lesser extent cation transport through the surface oxide film.
- compositions according to the present invention demonstrate many advantages over art-disclosed compositions including, without limitation, excellent strength; amenability to mass production techniques such as forming, joining and the like; and excellent resistance to oxidation under extreme conditions such as high temperatures.
- compositions of the present invention relate to the discovery that certain elements can be added to iron-base alloy materials to dramatically improve their resistance to oxidation. More particularly, the invention relates to the discovery that the addition of these elements (referred to herein as "dopants") yields materials suitable for use in heretofore impractical environments thereby avoiding the use of expensive, higher alloy-content materials.
- iron-base is meant that iron is the predominate alloy element present, by weight of the final composition.
- iron may be present at a level greater than any other single element by weight.
- Iron need not comprise 50 percent of the composition; by way of illustration (without limitation), a composition comprising 30 percent iron, by weight, and 29 percent nickel by weight, as well as other elements each being less than 30 percent by weight, but in aggregate totaling more than 50 percent by weight (including the nickel), would be iron-base as defined herein.
- Preferred alloy elements include those selected from the group consisting of silicon, nickel, chromium, cobalt, manganese, nitrogen, and mixtures thereof. Silicon, nickel, and chromium are particularly preferred.
- Iron as well as the alloy elements described above, can be employed at levels generally known in the art.
- the dopants of the present invention may be employed in AISI types 201, 202, 301, 302, 302B, 303, 303Se, 304, 304L, 305, 308, 309, 309S, 310, 315, 316, 316L, 317, 321, 347, 348, 384 and 385 austentic stainless steels.
- Employing the dopants of the present invention, in addition to the elements at levels conventionally employed (except for small modifications to maintain matrix stability, if needed) in such AISI materials produces materials which can then be employed in heretofore impossible or impractical environments or applications.
- compositions according to the present invention can also employ lower levels of strategic or expensive elements than generally disclosed in the art, but at the same time demonstrating equivalent or improved oxidation resistant properties.
- Stainless steel (RA 333) and non-stainless steel (INCO 330) may also employ the dopants of the present invention.
- Preferred compositions include those where nickel is present at a level of about 5 to about 15 percent, and where chromium is present at a level of about 10 to about 30 percent, by weight of the final composition.
- aluminum can play many roles in the compositions of the present invention. It can be used as an effective dopant when emploved a: levels below that at which it acts as a bulk oxide former.
- an alloy of this invention would be made with about 20 to 30 percent by weight chromium, about 0.1 to 1.5 percent by weight carbon, about 3 to 4 percent by weight manganese, about 0 to 12 percent by weight cobalt, about 5 to 15 percent by weight nickel and about 0.5 to 2 percent by weight dopant, with the balance being iron and normal residual impurities.
- the alloys of this invention can be described as oxidation resistance steels having iron as the base material with the addition of chromium and other alloying elements to increase oxidation resistance.
- the preferred alloys of this invention have a stable austenitic structure with the further feature that they contain minor quantities of dopant elements.
- Nickel, cobalt, nitrogen, carbon and manganese are strong austenite stabilizers in ferrous alloys and the concentration of one or more of these elements in the alloy should be maintained at a level high enough to ensure that the alloy's structure remains austenitic over the temperature range normally encountered by parts formed from the alloy.
- Alloying element ranges of 3 to 4 percent by weight, manganese; 5 to 15 percent by weight, nickel; 0 to 12 percent by weight, cobalt; 0.1 to 0.5 percent by weight, nitrogen; and 0.5 to 1.5 percent by weight, carbon provide good austenite stabilizing levels in normal ferrous alloys.
- Heat sizes were either 2500 or 5000 grams with resulting ingots weighing approximately 1800 grams. These ingots were hot forged and/or hot rolled into slabs with sufficient thermal-mechanical working to destroy the original cast microstructure. Hot and cold rolling, with inter-stage annealing was employed to produce final strip form, typically 0.030" thick. Special melting procedures were employed for the addition of Mg wherein Mg metal or NiMg was encased in iron foil and plunged into the melt to facilitate high recovery levels of Mg. For convenience, halogen salts of Li, Na, K, Mg, Ca were often employed for small quantity (less than 1 percent) additions of these elements.
- the magnesium dopant modified silicon-containing alloys show an average oxidation resistance improvement at 1204°C (2,200 degrees F) of 24 percent compared to the undoped base composition. Further addition of calcium dopant yields a 36 percent improvement compared to the undoped base composition.
- Introduction of Sodium, lithium, potassium, dopants, in addition to magnesium and calcium results in an average oxidation resistance improvement at 1204°C (2,200 degrees F) of 78 percent compared to the undoped base composition.
- Procedures used to evaluate experimental and commercial alloys range from simple still air cyclic oxidation tests with small coupons in laboratory furnaces, to vehicle tests with full size components.
- several of the following tests were performed: still-air cyclic oxidation in laboratory furnaces; cyclic endurance tests on engines loaded by dynamometers; controlled exhaust environment tests in tube furnaces; component endurance tests on engines loaded by dynamometers; and on-vehicle tests at the proving grounds for durability.
- Weight change data by itself can be quite misleading when comparing several different alloys if the mode of corrosive attack is not similar in each case.
- Metallography was used in most cases to supplement weight change data. Photomicrographs, therefore, are required to illustrate the point.
- Fig. 1 shown are graphs of the still-air cyclic oxidation resistance of LNA with other commercial high-temperature alloys at 1204°C (2200 degrees F),
- the LNA alloy outperforms the stainless steel (RA 333) and non-stainless steel (INCO 330) samples (commercial high nickel alloys marketed by Rolled Alloys and International Nickel, respectively) in exhibiting the least weight change over the cycles of testing.
- alloy test rings were utilized in various segments of an engine/dynamometer installation. Also employed were experimental alloy liners on exhaust manifolds of the engine driving the dynamometer.
- Fig. 3 is a schematic drawing of the alloy test ring pipe arrangement. The test conditions were controlled readily by injecting air at strategic points in the manifold, and adjusting carburetor jets to produce desired carbon monoxide levels and robot control of engine speed, load, spark and air injection.
- Mg, Ca, Li, Na and K are the active ingredients in this dopant concept
- other elements sucn as Y, Si and Al have shown second order interaction benefits with the dopants. While not intending to be bound by theory, this is thought to be due to their contribution to the formation of a stable host oxide along with the other active oxide formers such as chromium, nickel and iron.
- Both Al and Si are strong ferrite formers and their presence required the further addition of nitrogen as an austenitic stabilizer to maintain the required austenitic microstructure. Accordingly, aluminum can be effective as a dopant when employed at levels below those typically taught in the art and necessary to employ it as an oxide former.
- Fig. 7 illustrates the progressive improvement in cyclic oxidation resistance of the alloys of this invention as additional dopant elements were introduced.
- the final low nickel austenitic alloy, with oxidation resistance superior to commercial RA333 contained dopants from the group of elements Li, Na, K, Mg, Ca, Ba and La, all of which are found in Groups IA, IIA or IIIB of the Periodic Table of Elements.
- Fig. 7 summarizes the experimental-design development of these alloys.
- oxidation resistance is generally characterized by weight loss per unit area of a 0.030" thick test panel shown as the ordinate.
- the band “RA333” represents a common commercial oxidation resistant austenitic alloy used as the standard of reference in all oxidation tests.
- Tabulated along the abscissa are two rows of element designations.
- the "investigated” row identifies those elements selected by the fractional factorial experiment to be of potential interest and worthy of incorporation into detailed full factorial experimental schemes.
- the "accepted” row identifies those elements which were found to offer significant improvements in oxidation resistance following detailed analysis of full factorial experiments. Moving from left to right on Fig.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Powder Metallurgy (AREA)
- Heat Treatment Of Steel (AREA)
Claims (4)
- Eisenlegierungszusammensetzung mit verbessertem Widerstand gegenüber Oxidation enthaltend:(i) Eisen;(ii) mindestens ein Legierungselement, das aus der Gruppe ausgewählt ist, die aus Nickel, Chrom, Molybdän, Mangan, Silicium, Kohlenstoff, Vanadium, Kobalt, Kupfer, Stickstoff, Aluminium, Titan, Zirkon und Gemischen davon besteht;(iii) Magnesium als Dotierungselement in einem Anteil von 0,1 bis 1,5 Gew.-% der Endzusammensetzung;(iv) Calcium als Dotierungselement in einem Anteil von 0,1 bis 1,5 Gew.-% der Endzusammensetzung;(v) Lithium als Dotierungselement in einem Anteil von 0,1 bis 0,5 Gew.-% der Endzusammensetzung;(vi) Natrium als Dotierungselement in einem Anteil von 0,1 bis 0,5 Gew.-% der Endzusammensetzung; und(vii) Kalium als Dotierungselement in einem Anteil von 0,5 bis 1,0 Gew.-% der Endzusammensetzung.
- Zusammensetzung nach Anspruch 1, bei der das Legierungselement aus der Gruppe ausgewählt ist, die aus Silicium, Nickel, Chrom, Kobalt, Mangan, Stickstoff und Gemischen davon besteht.
- Zusammensetzung nach Anspruch 2, bei der Nickel in einem Anteil von 5 bis 15 Gew.-% der Endzusammensetzung vorliegt.
- Zusammensetzung nach Anspruch 2, bei der Chrom in einem Anteil von 10 bis 30 Gew.-% der Endzusammensetzung vorliegt.
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
PCT/US1988/000982 WO1989009843A1 (en) | 1988-04-04 | 1988-04-04 | Oxidation resistant iron base alloy compositions |
CA000563292A CA1340700C (en) | 1988-04-04 | 1988-04-05 | Oxidation resistant iron base alloy compositions |
Publications (3)
Publication Number | Publication Date |
---|---|
EP0366655A1 EP0366655A1 (de) | 1990-05-09 |
EP0366655A4 EP0366655A4 (en) | 1991-07-24 |
EP0366655B1 true EP0366655B1 (de) | 1996-02-28 |
Family
ID=33565659
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP88903643A Expired - Lifetime EP0366655B1 (de) | 1988-04-04 | 1988-04-04 | Bestandteile oxidationsbeständiger eisenlegierungen |
Country Status (4)
Country | Link |
---|---|
EP (1) | EP0366655B1 (de) |
CA (1) | CA1340700C (de) |
DE (1) | DE3855047T2 (de) |
WO (1) | WO1989009843A1 (de) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN107326293A (zh) * | 2017-06-02 | 2017-11-07 | 太仓市龙华塑胶有限公司 | 一种耐磨五金件 |
Families Citing this family (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
SE516583C2 (sv) * | 1997-12-05 | 2002-01-29 | Sandvik Ab | Austenitiskt rostfritt stål med god oxidationsbeständighet |
AUPP042597A0 (en) * | 1997-11-17 | 1997-12-11 | Ceramic Fuel Cells Limited | A heat resistant steel |
DE102008005803A1 (de) * | 2008-01-17 | 2009-07-23 | Technische Universität Bergakademie Freiberg | Bauteil aus höher kohlnstoffhaltigem austenitischem Stahlformguss, Verfahren zu deren Herstellung und deren Verwendung |
CN104032220B (zh) * | 2014-05-09 | 2016-05-25 | 无锡市华尔泰机械制造有限公司 | 一种高压临氢工况用法兰 |
US9896752B2 (en) | 2014-07-31 | 2018-02-20 | Honeywell International Inc. | Stainless steel alloys, turbocharger turbine housings formed from the stainless steel alloys, and methods for manufacturing the same |
US10316694B2 (en) | 2014-07-31 | 2019-06-11 | Garrett Transportation I Inc. | Stainless steel alloys, turbocharger turbine housings formed from the stainless steel alloys, and methods for manufacturing the same |
US9534281B2 (en) | 2014-07-31 | 2017-01-03 | Honeywell International Inc. | Turbocharger turbine housings formed from the stainless steel alloys, and methods for manufacturing the same |
DE102016005531A1 (de) * | 2016-05-02 | 2017-11-02 | Vladimir Volchkov | Niedriggekohlter Stahl |
Family Cites Families (34)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US648428A (en) * | 1898-10-01 | 1900-05-01 | Joseph Patrick | Alloy. |
US1653630A (en) * | 1922-02-25 | 1927-12-27 | Matthew G Collins | Alloy |
GB629859A (en) * | 1940-12-03 | 1949-09-29 | Egon Herbert Schwarz | Heat and acid resisting iron alloy |
GB803942A (en) * | 1956-05-04 | 1958-11-05 | Consett Iron Company Ltd | Improvements in or relating to mild steel |
US3017265A (en) * | 1959-09-25 | 1962-01-16 | Gen Electric | Oxidation resistant iron-chromium alloy |
SU212541A1 (ru) * | 1966-09-05 | 1968-02-29 | А. Л. Сотниченко , В. С. Ярковой | Коррозионностойкая сталь |
US3591371A (en) * | 1968-11-04 | 1971-07-06 | Cabot Corp | Cobalt base oxidation resistant alloy |
US3730779A (en) * | 1970-08-25 | 1973-05-01 | E Caule | Oxidation resistant iron base alloy |
US3676085A (en) * | 1971-02-18 | 1972-07-11 | United Aircraft Corp | Cobalt base coating for the superalloys |
BE787254A (fr) * | 1971-08-06 | 1973-02-05 | Wiggin & Co Ltd Henry | Alliages de nickel-chrome |
DE2161954A1 (de) * | 1971-12-14 | 1973-06-20 | Deutsche Edelstahlwerke Gmbh | Ferritischer hitzebestaendiger stahl |
JPS5631345B2 (de) * | 1972-01-27 | 1981-07-21 | ||
SU430186A1 (ru) * | 1972-11-29 | 1974-05-30 | М. Д. Цкитишвили , Ф. Н. Тавадзе Институт металлургии Грузинской ССР | Коррозионностойкая сталь |
SU441343A1 (ru) * | 1973-02-07 | 1974-08-30 | Центральный Научно-Исследовательский Институт Технологии Машиностроения | Жаростойка сталь |
SU475414A1 (ru) * | 1973-12-06 | 1975-06-30 | Центральный Научно-Исследовательский Институт Технологии Машиностроения | Нержавеюща сталь |
SU494429A1 (ru) * | 1974-04-17 | 1975-12-05 | Научно-Исследовательский И Опытноконструкторский Институт Автоматизации Черной Металлургии | Жаростойка сталь |
US4022587A (en) * | 1974-04-24 | 1977-05-10 | Cabot Corporation | Protective nickel base alloy coatings |
SU500288A1 (ru) * | 1974-07-23 | 1976-01-25 | Запорожский машиностроительный институт им.В.Я.Чубаря | Коррозионностойка сталь |
US4053308A (en) * | 1974-12-24 | 1977-10-11 | Howmedica, Inc. | Nonprecious alloy for fusion to porcelain |
SU589281A1 (ru) * | 1975-03-27 | 1978-01-25 | Центральный Научно-Исследовательский Институт Технологии Машиностроения | Жаростойка сталь |
SU553304A1 (ru) * | 1975-07-11 | 1977-04-05 | Институт Проблем Литья Ан Украинской Сср | Сплав на основе железа |
SU567769A1 (ru) * | 1976-04-19 | 1977-08-05 | Предприятие П/Я А-7476 | Сталь |
US4157923A (en) * | 1976-09-13 | 1979-06-12 | Ford Motor Company | Surface alloying and heat treating processes |
USRE31339E (en) * | 1977-08-03 | 1983-08-09 | Howmet Turbine Components Corporation | Process for producing elevated temperature corrosion resistant metal articles |
US4159908A (en) * | 1978-08-14 | 1979-07-03 | N L Industries, Inc. | Alkali metal containing battery grid lead alloy |
GB2036793B (en) * | 1978-12-02 | 1983-11-16 | Pells A | Nickl or nickelcobalt base alloys with corrosion resistance |
US4388125A (en) * | 1981-01-13 | 1983-06-14 | The International Nickel Company, Inc. | Carburization resistant high temperature alloy |
US4400211A (en) * | 1981-06-10 | 1983-08-23 | Sumitomo Metal Industries, Ltd. | Alloy for making high strength deep well casing and tubing having improved resistance to stress-corrosion cracking |
US4400209A (en) * | 1981-06-10 | 1983-08-23 | Sumitomo Metal Industries, Ltd. | Alloy for making high strength deep well casing and tubing having improved resistance to stress-corrosion cracking |
JPS59501828A (ja) * | 1982-10-05 | 1984-11-01 | イギリス国 | 改良アルミニウム合金 |
US4572750A (en) * | 1983-07-21 | 1986-02-25 | The Foundation: The Research Institute Of Electric And Magnetic Alloys | Magnetic alloy for magnetic recording-reproducing head |
US4600556A (en) * | 1983-08-08 | 1986-07-15 | Inco Alloys International, Inc. | Dispersion strengthened mechanically alloyed Al-Mg-Li |
KR860700360A (ko) * | 1984-11-05 | 1986-10-06 | 제. 뻬. 죠르쥬 | 금속 및 합금의 정련 처리공정 |
US4612166A (en) * | 1985-10-15 | 1986-09-16 | Olin Corporation | Copper-silicon-tin alloys having improved cleanability |
-
1988
- 1988-04-04 EP EP88903643A patent/EP0366655B1/de not_active Expired - Lifetime
- 1988-04-04 DE DE3855047T patent/DE3855047T2/de not_active Expired - Fee Related
- 1988-04-04 WO PCT/US1988/000982 patent/WO1989009843A1/en active IP Right Grant
- 1988-04-05 CA CA000563292A patent/CA1340700C/en not_active Expired - Fee Related
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN107326293A (zh) * | 2017-06-02 | 2017-11-07 | 太仓市龙华塑胶有限公司 | 一种耐磨五金件 |
Also Published As
Publication number | Publication date |
---|---|
EP0366655A4 (en) | 1991-07-24 |
EP0366655A1 (de) | 1990-05-09 |
WO1989009843A1 (en) | 1989-10-19 |
DE3855047T2 (de) | 1996-09-12 |
CA1340700C (en) | 1999-08-10 |
DE3855047D1 (de) | 1996-04-04 |
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