Steel alloy having improved creep strength

Abstract

An austenitic steel alloy is provided having improved creep strength at high temperature. The improved creep strength performance is achieved by adding a limited amount of silicon to the steel alloy along with increased amounts of nitrogen and columbium, also known as niobium. The added columbium ties up the carbon in the alloy composition to prevent sensitization promotion and premature corrosion-fatigue failures. The resulting steel alloy provides improved strength, improved carburization resistance, and maintains good weldability.

Description

BACKGROUND OF THE INVENTION

1. Field of the Invention

The present invention relates to an austenitic steel having improved creep strength.

2. Description of the prior art

Recent developments in the formulation of austenitic steel alloys have produced austenitic steels having desired properties such as high temperature oxidation resistance, good cold workability, weldability and high mechanical strength at ambient temperature. Research continues, however, into providing a steel alloy having improved creep strength, which is useful for steel annealing box covers which operate at temperatures around 800.degree. C.

Recently, Avesta has developed a new alloy grade designated Avesta 253MA.TM. which provides improved creep strength over its prior steel alloys. This development is discussed in U.S. Pat. No. 4,224,062. Therein, an austenitic steel alloy having improved high temperature creep strength is formed by incorporating a rare earth metal, such as lanthanum and the other lanthanides, and an alkaline earth metal, such as the group 2a elements calcium, strontium and barium, into a fully austenitic steel. In a preferred embodiment, calcium in the amount 0.002-0,006 % by weight is used as the alkaline earth metal and cerium in the amount 0.03-0.07 % by weight is used as the rare earth metal. Even with the improved creep strength afforded by the alloy disclosed in U.S. Pat. No. 4,224,062, alloy 253MA.TM. provides only a marginal improvement in creep strength over existing steel alloys.

Table I below sets forth the expected average creep strain at 700.degree. C. for 253MA.TM. steel alloy and 309 steel alloy, an existing austenitic steel alloy recognized as needing improved creep performance. As can be seen, even with the addition of the lanthanide rare earth metals and alkaline earth metals, the increased creep strain performance of 253MA.TM. steel alloy is minimal.

TABLE I______________________________________Creep Strain At 700.degree. C. (MPa) 253 MA .TM. 309______________________________________ 1,000 hours 74 7010,000 hours 44 40______________________________________

Although the addition of a lanthanide rare earth metal performs satisfactorily in the 253MA.TM. alloy, the addition of a lanthanide metal lessens the weldability of certain alloy compositions. Notably, the addition of a rare earth lanthanide metal to alloy 309 results in an alloy having lessened weldability performance. Thus, there is a need for an alloy having improved creep strength which does not rely on the addition of a rare earth metal to provide that improved property.

It is also desired in a steel alloy to have improved carburization resistance. The typical approach to improve carburization resistance is to increase the amount of silicon in the steel alloy. However, the addition of silicon to most austenitic steel alloys reduces the creep strength of the alloys and worsens fusion cracking in the weldments in the alloys. Consequently, there is a need for a steel alloy having improved carburization resistance which does not rely on the addition of higher silicon content in the alloy composition.

SUMMARY OF THE INVENTION

An austenitic steel alloy is provided having improved creep strength properties without sacrificing carburization resistance and weldability performance. This improved alloy is characterized by the addition of a limited amount of silicon along with nitrogen and columbium, also known as niobium. The new steel alloy has the general composition of the 309 alloy with the silicon concentration changed to approximately 1.50 percent, the nitrogen concentration being approximately 0.15 percent, and the columbium concentration being approximately 0.40 percent. Such a steel alloy composition provides improved creep strength over the 309 alloy, maintains the weldability performance of the 309 alloy and has about three times the carburization resistance of the 309 steel alloy.

DESCRIPTION OF THE DRAWINGS

FIG. 1 is a graph showing the creep strength of the steel alloy made in accordance with the present invention compared with prior art steel alloys as a function of temperature and time.

DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS

An improved steel alloy, designated as alloy JL349.TM., is provided having enhanced creep strength performance and carburization resistance. The composition of the improved steel alloy is similar to the formulation of the 309 alloy with the addition of silicon, nitrogen and columbium. A presently preferred version of the alloy having the fellowing weight percent composition is set forth in Table II below.

TABLE II______________________________________carbon 0.050 nickel 14.55manganese 1.55 molybdenum 0.50phosphorus as low as possible copper 0.50sulfur 0.001 nitrogen 0.15silicon 1.50 columbium 0.40chromium 23.20 boron 0.0015______________________________________

The expected average creep performance of this improved alloy grade shows a creep strain of 120MPa at 700.degree. C. for 1,000 hours and 90MPa creep strain at 700.degree. C. for 10,000 hours. This creep performance is significantly improved compared to the estimated average creep performance of the prior art 253MA.TM. and 309 grade see forth in Table I above.

The presently preferred steel alloy JL349.TM. has a ferrite content of 4.5 percent based on the Delong diagram. Using the WRC 1992 and WRC 1988 diagrams, the ferrite concentration of the proposed steel alloy is extrapolated to 3.5 percent.

Tests were performed on the improved steel alloy JL349.TM. in accordance with the present invention as well as the prior are 309 grade alloy and 253MA.TM. grade alloy. Results of those tests are set forth in Table III below in which the temperature, the time for 1% creep, the creep strain, the log stress and the Larson-Miller Parameter are reported.

TABLE III______________________________________ 1% Creep Temp Time Stress Log L-MTest Alloy (.degree.F.) (sec) (MPa) Stress Prm.______________________________________1 309 1652 14.35 13.1 1.117 446832 309 1652 23.26 13.1 1.117 451263 309 1652 14.64 13.1 1.117 447024 JL349 .TM. 1292 19231 53.1 1.725 425465 JL349 .TM. 1292 34480 39.3 1.594 429908 253MA .TM. 1652 5128 13.1 1.117 5007510 JL349 .TM. 1472 12500 26.2 1.418 4655511 253MA .TM. 1652 7407 13.1 1.117 5041312 253MA .TM. 1652 4545 10.3 1.013 4996513 JL349 .TM. 1652 227 10.3 1.013 4721614 JL349 .TM. 1652 26.7 13.1 1.117 45253______________________________________

The creep data for the 253MA.TM. steel alloy matches the published data for that alloy reasonably well.

The Larson-Miller Parameter is an empirical number reflecting the operating temperature and the creep strength of the alloy. The Larson-Miller Parameter is defined in accordance with the equation below:

L-M=(T+460)*(log(t)+20 where T is the test temperature in degrees Fahrenheit and t is the time in hours for 1 percent creep to occur at the operating temperature.

Table III shows that the performance of improved steel alloy JL349.TM. is superior to that of prior art steel alloy 309 through operating temperatures up to 800.degree. C. (1472.degree. F.). At operating temperatures above 800.degree. C., the performance of improved steel alloy JL349.TM. reverts to that of alloy 309. Thus, when used in operating conditions under 800.degree. C., such as in an annealing box, improved steel alloy JL349.TM. provides improved creep strength over prior art steel alloys.

The results of the data in Table III have been plotted in FIG. 1. FIG. 1 also includes data regarding published information concerning the 253MA.TM. alloy. FIG. 1 shows that the improved steel alloy JL349.TM. of the present invention achieves improved creep strength.

Columbium is added to the formulation of improved steel alloy JL349.TM. to tie up the carbon which is present in the alloy composition. In alloy 309 and the 253MA.TM. alloy, the carbon is not tied up. As a result, the carbon in these alloys promotes sensitivization and premature corrosion-fatigue failures. By the addition of columbium, improved steel alloy JL349.TM. overcomes the sensitivization promotion and premature corrosion-fatigue failures of the other alloys.

The improved steel alloy JL349.TM. of the present invention provides its improved creep strength performance without sacrificing carburization resistance. Table IV below presents carburization data obtained for improved steel alloy JL349.TM. of the present invention, as well as alloy 309S and alloy 253MA.TM.. This carburization data was obtained by exposing the subject material to an endothermic atmosphere of 40% N.sub.2, 21% CO, 40% H.sub.2 and 1% CH.sub.4 at 1700.degree. F. for 5 cycles, 12 hours each.

TABLE IV______________________________________ Weight GainMaterial Condition (mg/sq. in.) % C______________________________________309S As received -- .042309S Carburized 6.5 .105309S Carburized 6.8 .106253MA .TM. As received -- .090253MA .TM. Carburized 7.4 .141253MA .TM. Carburized 6.7 .127JL349 .TM. As received -- .051JL349 .TM. Carburized 4.4 .050JL349 .TM. Carburized 4.2 .051______________________________________

As the data in Table IV above demonstrates, alloy JL349.TM. of the present invention shows less weight gain and less added carbon after exposure to a carburizing atmosphere than do prior art alloys.

In the foregoing specification certain preferred practices and embodiments of this invention have been set out, however, it will be understood that the invention may be otherwise embodied within the scope of the following claims.

Claims

1. An austenitic steel, said austenitic steel having improved creep strength at temperatures below 800.degree. C. and consisting essentially of the following alloying elements:

C:0.10%

Si:more than 1% but not greater than 2%

Mn:not greater than 3%

Cr:15-25%

Ni:10-18%

Cb:more than 0.20%, but not greater than 0.75%

N:more than 0.10%, but not greater than 0.25%

Mo:less than 1%

B:greater than 0.001%, but less than 0.0025%, the amounts of said alloying elements being adjusted to result in an austenitic microstructure, and a balance of iron and other nonessential elements and impurities.

2. An austenitic steel, said austenitic steel having improved creep strength and consisting essentially of the following alloying elements:

C:less than 0.10%

Mn:greater than 1%, but less than 2%

S:less than 0.003%

Si:greater than 1%, but less than 2%

Cr:greater than 15%, but less than 25%

Ni:greater than 10%, but less than 20%

Mo:less than 1%

Cu:less than 1%

N:greater than 0.10%, but less than 0.20%

Cb:greater than 0.20%, but less than 0.75%

B:greater than 0.001%, but less than 0.0025% the amount of said alloying elements being adjusted to result in an austenitic microstructure; and balance of iron and impurities.

3. The alloy of claim 2, wherein Cr is 20-25% and Ni is 12-16%.

4. The austenitic steel of claim 3 wherein Si is 1.25%-1.75% and Cb is 0.30%-0.50%.

5. The austenitic steel of claim 4 wherein Si is approximately 1 50% N is approximately 0.15% and Cb is approximately 0.40%.