Austenitic stainless steel with good oxidation resistance

Abstract: A new austenitic stainless steel alloy is provided according to the following analysis: C: < 0,12, Si: < 1,0, Cr: 16-22, Mn: < 2,0, Ni: 8-14, Mo: < 1,0, either Ti: > 4·% by weight of C and < 0,8 or Nb: 8·% by weight of C and < 1,0, S: < 0,03, O: < 0,03, N: < 0.05, La: ≥ 0,02 and ≤ 0,11, and the remainder Fe and normally occurring impurities. The new steel is particularly suitable as super heater steel and heat exchanger steel.

Description: The present invention relates to an austenitic stainless steel according to claim 1. It has a particularly good oxidation resistance in applications as a superheater steel, such as for instance in conventional carbon boilers. High demands for a good oxidation and corrosion resistance, strength at increased temperatures and structural stability, are made on materials that are used in high temperature applications. Structural stability implies that the structure of the material during operation shall not degenerate into fragility-causing phases. The choice of material depends on the temperature and the load, and of course on the cost. By oxidation resistance, which is of considerable importance for the present invention, is in high temperature contexts meant the resistance of the material against oxidation in the environment to which it is subjected. Under oxidation conditions, i.e., in an atmosphere that contains oxidizing gasses (primarily oxygen and water vapour), an oxide layer is formed on the steel surface. When the oxide layer attains a certain thickness, oxide flakes detach from the surface, a phenomenon called scaling. With scaling, a new metal surface is exposed, which also oxidizes. Thus, by the fact that the steel is continuously transformed into its oxide, its load-carrying capability will gradually deteriorate. The scaling may also result in other problems. In superheater tubes, the oxide flakes are transported away by the vapour and if accumulations of these flakes are formed in, e.g., tube bends, the vapour flow in the tubes may be blocked and cause a break-down because of overheating. Further, the oxide flakes may cause so called solid particle erosion in the turbine system. Scaling may also cause great problems in a boiler, which manifest themselves in the form of a lower effect, unforeseen shutdowns for repairs and high repairing costs. Smaller scaling problems render it possible to run the boiler with a higher vapour temperature, which brings about an increased power economy. Thus, a material with good oxidation resistance shall have a capability of forming an oxide that grows slowly and that has a good adhesion to the metal surface. The higher the temperature that the material is subjected to, the stronger is the oxide formation. A measure of the oxidation resistance of the material is the so called scaling temperature, which is defined as the temperature at which the oxidation-related loss of material amounts to a certain value, for instance 1,5 g/m 2 ·h. A conventional way to improve the oxidation resistance is to add chromium, which contributes by giving to the material a protective oxide layer. At increased temperature, the material is submitted to deformation by creep. An austenitic basic mass, which is obtained by addition of an austenite stabilizing substance such as nickel, influences favourably the creep strength, as does precipitations of a minute secondary phase, for instance carbides. The alloying of chromium into steel brings about an increased tendency to separate the so called sigma phase, which may be counteracted by, as indicated above, the addition of austenite stabilizing nickel. Both manganese and nickel have a positive influence on the structure stability of the material. Both these elements function as austenite-stabilizing elements, i.e., they counteract the separation of fragility causing sigma phase during operation. Manganese also improves the heat check resistance during welding, by binding sulphur. Good weldability constitutes an important property for the material. Austenitic stainless steels of the type 18Cr-10Ni have a favourable combination of these properties and are therefore often used for high temperature applications. A frequently occurring alloy of this type is SS2337 (AISI Type 321), corresponding to Sandvik 8R30. The alloy has a good strength, thanks to the addition of titanium, and a good corrosion resistance, so it has for many years been used in, e.g., tubes for superheaters in power plants. However, the weakness of this alloy is that the oxidation resistance is limited, which brings about limitations with regard to operable life and maximum temperature of use. Same type of alloys have been modified with addition of REM (one or more of Ce, La, Pr, Nd), where 0.10% <REM≤0.3 for high temperature oxidation resistance improvement in the disclosure WO 97/31130. The Soviet inventor's certificate SU 1 038 377 discloses a steel alloy which is said to be resistant to stress corrosion, primarily in a chlorine-containing environment. However, this type of problem concerns substantially lower temperatures than superheater applications. It contains (in % by weight) 0,03 - 0,08 C, 0,3 - 0,8 Si, 0,5 - 1,0 Mn, 17 - 19 Cr, 9 - 11 Ni, 0,35 - 0,6 Mo, 0,4 - 0,7 Ti, 0,008 - 0,02 N, 0,01 - 0,1 Ce and the remainder Fe. Moreover, e.g., its heat check resistance and weldability are unsatisfactory. Thus, a primary object of the present invention is to provide a steel of the type 18Cr-10Ni that has a very good oxidation resistance, and thereby an extended life, at high temperature applications, primarily in a vapour environment. A second object of the present invention is to provide a steel of the type 18Cr-10Ni that has an increased maximum temperature of use. These and further objects have been attained in a surprising way by providing a steel sort according to the analysis as defined in claim 1. The present invention consists of a modified and improved variant of the prior art alloy SS2337, which may have a commercial analysis in weight % as follows: C 0,04 - 0,08 Si 0,3 - 0,7 Mn 1,3 - 1,7 P max 0,040 S max 0,015 Cr 17,0 - 17,8 Ni 10,0 - 11,1 Mo max 0,7 Ti max 0,6 Cu max 0,6 Nb max 0,05 N max 0,050 The essential feature of the present invention is that one adds a rare earth metal, that is pure lanthanum, to an alloy which basically corresponds to SS2337 above, however with the exception that the interval for some of the elements may be widened. This addition of pure La has resulted in a surprisingly good oxidation resistance in air as well as water vapour, and maintained good strength and corrosion properties. Extensive investigations have shown that the range 0,02 % by weight < La ≤ 0,11 % by weight is optimal with regard to oxidation properties and hot workability. Without being bound by any underlying theory, the improvement of the oxidation properties is considered to depend upon the content of rare earth metal solved in the steel, wherefore it is important to keep down the contents of elements such as S, O and N. Underneath follows a listing of the ranges of each element: Carbon contributes together with Ti to give the material sufficient creep strength. Too high amounts result in a precipitation of chromium carbides, which has two negative effects: a) Precipitation of carbides at grain borders brings about an increased risk of intercrystalline corrosion, i.e., the material is sensitized. b) The chromium carbides bind chromium, which deteriorates the oxidation resistance of the material. Of these reasons, a carbon content is chosen of max. 0,12 % by weight, preferably max. 0,10 % by weight and in particular between 0,04 and 0,08 % by weight. Silicon contributes to a good weldability and castability. Too high silicon contents cause brittleness. Therefore, a silicon content of max.1,0 % b.w. is suitable, preferably max 0,75 % b.w. and in particular between 0,3 and 0,7 % b.w. Chromium contributes to a good corrosion and oxidation resistance. However, chromium is a ferrite stabilizing element and too high a content of Cr brings about an increased risk of embrittlement by the creation of a so called σ-phase. Of these reasons, a chromium content of between 16 and 22 % b.w. is chosen, preferably between 17 and 20 % b.w. and in particular between 17 and 19 % b.w. Manganese has a high affinity to sulphur and forms MnS. At production, this makes that the workability is improved and for welding, an improved resistance is obtained to the formation of heat checks. Further, manganese is austenite stabilizing, which counteracts any embrittlement. On the other hand, Mn contributes to a high alloy cost. Of these reasons, the manganese content is suitably set between 1,3 and 1,7 % b.w. Nickel is austenite stabilizing and is added to obtain an austenitic structure, which gives an improved strength and counteracts embrittlement. However, equally to manganese, nickel contributes to a high alloy cost. Of these reasons, the nickel content is suitably set to between 8 and 14 % b.w., preferably of between 9,0 and 13,0 % b.w., and in particular to between 9,5 and 11,5 % b.w. Molybdenum favours the precipitation of embrittling σ-phase. Therefore, the Mo content should not exceed 1,0 % b.w. Titanium has a high affinity to carbon and by the formation of carbides improved creep strength is obtained. Also Ti in solid solution contributes to good creep strength. The fact that Ti binds carbon also decreases the risk of separation of chromium carbide in the grain borders (so called sensitizing). On the other hand, too high a Ti content causes brittleness. Of these reasons, the Ti content should be higher than four times the carbon content, and not be equal or exceed 0,80 % b.w. Alternatively, the steel may be stabilized by niobium instead of by titanium. With the same arguments as for titanium, it applies that the niobium content should not be less than 8 times the carbon content, and not be equal or exceed 1,0 % b.w. Oxygen, nitrogen and sulphur normally binds the chosen rare earth metal in the form of oxides, nitrides and sulphides, whereby these do not contribute to an improved oxidation resistance. Of these reasons, each one of the S and O contents should not exceed 0,03 % b.w., and the N content not 0,05 % b.w. Preferably, the S and the O content should not exceed 0,005 % b.w. and the N content not 0,02 % b.w. Lanthanum improves, as mentioned above, the oxidation resistance, also in small amounts. Below a certain concentration this effect is not apparent. No further improvement of the oxidation resistance is achieved after the addition above a certain limit. Of these reasons, the lanthanum content is suitably chosen to between 0,05-0,10 % b. w.. Melts of SS2337 with different contents of rare earth metals were produced by melting in a HF oven and casting into ingots. The chemical composition is shown in the following Table 1. From the ingots 10 mm thick plates were sawn across the ingot, which plates then were hot-rolled to a thickness of about 4 mm. The object of this procedure was to break down the cast structure and obtain an even grain size. At the same time an indication is obtained of the hot workability of the alloy. The rolled plates were then annealed according to the practice for this steel type, which means a holding time of 10 minutes at 1055°C, followed by water quenching. Charge nr 654629 654695 654699 654705 654710 654696 C % 0,078 0,063 0,067 0,064 0,063 0,063 Si % 0,39 0,40 0,42 0,42 0,40 0,40 Mn % 1,49 1,44 1,53 1,51 1,46 1,48 P % 0,023 0,024 0,025 0,024 0,023 0,023 S ppm 6 12 10 5 9 5 Cr % 17,32 17,42 17,34 17,31 17,51 17,47 Ni % 10,11 10,26 10,17 10,17 10,15 10,19 Mo % 0,19 0,26 0,26 0,25 0,25 0,26 Ti % 0,51 0,42 0,45 0,41 0,43 0,41 N % 0,008 0,009 0,010 0,010 0,011 0,011 Ce % <0,01 <0,01 <0,01 0,11 <0,01 0,05 La % <0,005 <0,005 0,11 <0,005 0,05 <0,005 Nd % <0,005 <0,005 <0,005 <0,005 <0,005 <0,005 Pr % <0,005 <0,005 <0,005 <0,005 <0,005 <0,005 REM* % <0,01 <0,01 0,11 0,11 0,05 0,05 O ppm 22 31 31 29 54 62 For the oxidation testing, rectangular so called oxidation coupons were cut out in a size of 15 x 30 mm, whose surface was ground with a 200 grain grinding paper. The assays were then oxidized during 3000 h in water vapour at 700°C. The result may be seen in Fig. 1, where the weight change during oxidation in water vapour has been plotted as a function of testing time. In Fig. 1 may be seen that for SS2337 without any rare earth metals (charge 654695), the weight diminishes after 1000 h in vapour at 700°C, which means that the material peels, i.e., oxide flakes fall off. For the charges that have been alloyed with pure lanthanum and with other rare earth metals, only a weak weight increase takes place, which indicates that the material forms an oxide with good adhesion. As mentioned above, this is a desirable property for alloys that are used in superheater tubes. An investigation was performed in order to find out the influence on the hot workability properties for the rare earth metals Ce and La. Charges were produced according to the procedure described above and were subsequently hot tensile tested at different temperatures. The results in Fig. 2 show that lanthanum does not have a negative effect on hot workability, which is the case with Ce. The improvement of the oxidation properties comes from the content of La present in solution in the steel. Elements such as sulphur, oxygen and nitrogen react easily with La already in the steel melt and forms stable sulphides, oxides and nitrides. La bound in these compounds is therefore not credited to the oxidation properties, wherefore the S, O and N contents should be kept low. A performed creep assay demonstrates no impaired creep strength for the rare earth metal alloyed material.

Claims: Austenitic stainless steel, characterized in the following analysis in % by weight: C < 0,12, Si < 1,0, Cr 16-22, Mn 1,3 - 1,7, Ni 8-14, Mo < 1,0, either Ti > 4 x % by weight of C and < 0,8 or Nb 8 x % by weight of C and < 1,0, S < 0,03, O < 0,03, N < 0.05, La ≥0,05 and ≤ 0,10, and the remainder Fe and unaviodable impurities. Steel according to claim 1, characterized in, that the carbon content is between 0,04 and 0,08 % b.w. Steel according to claim 1 or 2, characterized in, that the silicon content is between 0,3 and 0,7 % b.w. Steel according to claims 1-3, characterized in, that the chromium content is between 17 and 20 % b.w. Steel according to claims 1-4, characterized in, that the nickel content is between 9,0 and 13,0 % b.w. Use of a steel according to any of claims 1-5 as superheater steel, as for instance in carbon boilers. Use of a steel according to any of claims 1-5 as heat exchanger steel. Use of a steel according to any of claims 1-5 as heat exchanger steel in the convection part of an ethene oven.

Inventors: LINDEN JOHAN, LINDEN, JOHAN, Lindén, Johan
Applicants: SANDVIK AB, SANDVIK AKTIEBOLAG
Application year: 1998
Main classification: C22C38
IPC codes: F28F21, C22C38