Ferritic martensitic iron based alloy, a component and a process

Abstract

A novel ferritic martensitic alloy is provided. The ferritic martensitic alloy enables the use temperature to be increased from 500° C. to 550° C., where the strength is maintained or is even maximized and the toughness, especially for low temperatures, is maintained compared to the known iron-based alloys. Tunsten is preferably not used.

Description

CROSS REFERENCE TO RELATED APPLICATIONS

This application is the US National Stage of International Application No. PCT/EP2009/003640, filed May 22, 2009 and claims the benefit thereof.

FIELD OF INVENTION

The invention relates to a ferritic-martensitic alloy, to a component and to a process.

BACKGROUND OF INVENTION

Iron-based alloys are inexpensive alloys compared to nickel-based superalloys, but the strengths and toughnesses thereof are lower compared to the nickel-based superalloys.

Similarly, EP 1 466 993 B1 is known, in which use is made of tungsten.

SUMMARY OF INVENTION

It is therefore an object of the invention to propose an alloy by means of which the use temperature can be increased, and at the same time the strength is maximized and the toughness is retained especially for lower temperatures.

The object is achieved by an alloy as claimed in the claims, by a component as claimed in the claims and by a process as claimed in the claims.

The dependent claims list further advantageous measures which can be combined with one another, as desired, to achieve further advantages.

BRIEF DESCRIPTION OF THE DRAWINGS

FIGS. 1, 2, 3 show exemplary embodiments, and

FIG. 4 shows a steam turbine.

The figures and the description represent merely exemplary embodiments of the invention.

DETAILED DESCRIPTION OF INVENTION

The prior art is formed by iron-based alloys, known from EP 0 867 523, in which use is made of tungsten.

With preference, the new ferritic-martensitic alloy dispenses with the addition of tungsten (W) except for the customary impurities, which lie considerably below 0.1% by weight, in particular below 0.01% by weight.

The tables in FIGS. 1 to 3 show some exemplary embodiments of the invention.

The iron-based alloy comprises, in an inconclusive list (in % by weight):

• carbon (C): 0.13-0.22,
• chromium (Cr): 9.0-9.8,
• molybdenum (Mo): 1.0-2.0, in particular 1.4-1.6,
• nickel (Ni): 0.3-0.8, in particular 0.3-0.7,
• vanadium (V): 0.25-0.35, in particular 0.25-0.3,
• aluminum (Al): 0.005-0.01,
• niobium (Nb): 0.04-0.06,
• boron (B): 20 ppm-70 ppm, in particular 35 ppm-55 ppm,
• nitrogen (N): 150 ppm-500 ppm,
• cobalt (Co): 0-1.5, in particular up to 1.3,
• manganese (Mn): 0-0.15,
• silicon (Si): 0-0.1,
• phosphorus (P): 0-0.005,
• sulfur (S): 0-0.003,
• arsenic (As): max. 0.015,
• tin (Sn): max. 0.015,
• antimony (Sb): max. 0.015,
• copper (Cu): max. 0.1,
• iron (Fe).

The alloy preferably consists of these elements.

The boron content gives rise to a very good long-term stability at elevated temperatures. Here, the boron content is optimized with the required nitrogen content, in order to avoid the formation of boron nitrides. This gives rise to a good balance of strength and toughness.

Boron stabilizes the microstructure by incorporation in chromium-based M23C6 carbides and reduces the growth of the M23C6 carbides, as a result of which a high microstructure stabilization and consequently creep rupture strength are achieved.

It has been established that tungsten must not be used in order to achieve a high long-term stability with good long-term toughness. As a result, the toughnesses do not change depending on the temperature and time.

Tungsten is preferably not added since, although tungsten acts as a solid solution hardener, in the long term tungsten is precipitated as a Laves phase and then also coarsens quicker than other particles and therefore no longer participates in the stabilization of the particles of the microstructure.

In addition, the long-term toughness can be impaired by tungsten at temperatures <550° C.

The nickel content gives rise to a good forgeability.

The nickel content is lowered owing to the fact that the creep rupture strength is improved by reducing the diffusion coefficients in the microstructure.

The changed ability to achieve full hardening is compensated for by the addition of carbon (C) and cobalt (Co).

The content of carbon (C) is lowered owing to the balance with other elements for achieving a martensite microstructure with a high toughness. The lowered carbon content makes it possible for the austenite to be completely converted upon cooling to room temperature (no residual austenite), as a result of which a high microstructure homogeneity, a good martensite lath structure, a high toughness and a fine carbide formation of M23C6 are achieved, and therefore a good creep rupture strength is achieved. Carbon is required for the formation of M23C6. It is advantageous to use carbon contents >0.13% by weight.

Nitrogen forms MX particles (VN, VCC, N) Nb(C, N) for hardening the particles of the martensite microstructure based on (V, Nb)N, as a result of which the creep rupture strength is increased (MX stands for precipitations of the form VN, V(C, N) Nb(C, N).

It is advantageous to use nitrogen contents >150 ppm.

The silicon content is lowered since this improves the long-term toughness and reduces the nucleation for Laves phase precipitation (see under tungsten).

The manganese content is lowered owing to the positive effect on the increase in the creep rupture strength by increasing the Ac1 temperature, as a result of which it is possible to achieve a higher use temperature without influencing the microstructure or without a ferrite/martensite-austenite microstructure conversion:

Ac1 is the conversion temperature from ferrite to austenite; in the time/temperature conversion graph, “Ac1” is the first conversion point when heating the material. It denotes the start of the alpha-gamma conversion (start of the austenite formation).

The proportions of phosphorus, sulfur and copper are lowered in order to improve the initial toughness of the microstructure and to ensure a high long-term toughness.

It is preferable not to use titanium, since otherwise nitrogen would become bonded as TiN and therefore the MX particles of the form (V,Nb)N which are required for the creep rupture strength would be absent.

The use temperature for components is increased by this alloy, with the toughness/ductility being retained at relatively low temperatures.

The minimum contents in the claims are in each case preferably

• 0.1% by weight for cobalt (Co),
• 0.01% by weight for silicon (Si),
• 0.001% by weight for phosphorus (P),
• 0.05% by weight for manganese (Mn),
• 0.01% by weight for copper (Cu);
  these lie considerably above the detection limits for these elements and the degree of impurity thereof.

FIG. 2 illustrates a steam turbine 300, 303 with a turbine shaft 309 extending along an axis of rotation 306.

The steam turbine has a high-pressure part-turbine 300 and a medium-pressure part-turbine 303, each having an inner housing 312 and an outer housing 315 surrounding the inner housing. The high-pressure part-turbine 300 is, for example, of pot-like design. The medium-pressure part-turbine 303 is, for example, of two-flow design. It is also possible for the medium-pressure part-turbine 303 to be of single-flow design.

Along the axis of rotation 306, a bearing 318 is arranged between the high-pressure part-turbine 300 and the medium-pressure part-turbine 303, the turbine shaft 309 having a bearing region 321 in the bearing 318. The turbine shaft 309 is mounted on a further bearing 324 next to the high-pressure part-turbine 300. In the region of this bearing 324, the high-pressure part-turbine 300 has a shaft seal 345. The turbine shaft 309 is sealed with respect to the outer housing 315 of the medium-pressure part-turbine 303 by two further shaft seals 345. Between a high-pressure steam inflow region 348 and a steam outlet region 351, the turbine shaft 309 in the high-pressure part-turbine 300 has the high-pressure rotor blading 357. This high-pressure rotor blading 357, together with the associated rotor blades (not shown in more detail), constitutes a first blading region 360.

The medium-pressure part-turbine 303 has a central steam inflow region 333. Assigned to the steam inflow region 333, the turbine shaft 309 has a radially symmetrical shaft shield 363, a cover plate, on the one hand for dividing the flow of steam between the two flows of the medium-pressure part-turbine 303 and also for preventing direct contact between the hot steam and the turbine shaft 309. In the medium-pressure part-turbine 303, the turbine shaft 309 has a second blading region 366 having the medium-pressure rotor blades 354. The hot steam flowing through the second blading region 366 flows out of the medium-pressure part-turbine 303 from an outflow connection piece 369 to a low-pressure part-turbine (not shown) which is connected downstream in terms of flow.

The turbine shaft 309 is composed, for example, of two turbine part-shafts 309a and 309b, which are fixedly connected to one another in the region of the bearing 318. Each turbine part-shaft 309a, 309b has a cooling line 372 fanned as a central bore 372a along the axis of rotation 306. The cooling line 372 is connected to the steam outlet region 351 via an inflow line 375, which has a radial bore 375a. In the medium-pressure part-turbine 303, the coolant line 372 is connected to a cavity (not shown in more detail) beneath the shaft shield. The inflow lines 375 are designed as a radial bore 375a, with the result that “cold” steam from the high-pressure part-turbine 300 can flow into the central bore 372a. Via the outflow line 372, which is in particular also designed as a radially oriented bore 375a, the steam passes through the bearing region 321 into the medium-pressure part-turbine 303, where it then passes onto the lateral surface 330 of the turbine shaft 309 in the steam inflow region 333. The steam flowing through the cooling line is at a significantly lower temperature than the reheated steam flowing into the steam inflow region 333, so that effective cooling of the first rotor blade rows 342 of the medium-pressure part-turbine 303 and of the lateral surface 330 in the region of these rotor blade rows 342 is ensured.

Claims

1-33. (canceled)

34. An iron-based alloy, comprising (in % by weight):

carbon 0.13-0.22;

chromium 9.0-9.8;

molybdenum 1.0-2.0;

nickel 0.3-0.8;

vanadium 0.25-0.35;

aluminum 0.005-0.01;

niobium 0.04-0.06;

boron 20 ppm-70 ppm;

nitrogen 150 ppm-500 ppm;

cobalt 0-1.5;

manganese 0-0.15;

silicon 0-0.1;

phosphorus 0-0.005;

sulfur 0-0.003;

arsenic 0-0.015;

tin 0-0.015;

antimony 0-0.015;

copper 0-0.1; and

remainder iron.

35. The alloy as claimed in claim 34, wherein the alloy comprises at most 0.18% by weight carbon.

36. The alloy as claimed in claim 34, wherein the alloy comprises at least 0.18% by weight carbon.

37. The alloy as claimed in claim 34, wherein the alloy comprises at least 9.3% by weight chromium.

38. The alloy as claimed in claim 34, wherein the alloy comprises at most 9.4% by weight chromium.

39. The alloy as claimed in claim 34, wherein the alloy comprises at least 0.5% by weight nickel.

40. The alloy as claimed in claim 34, wherein the alloy comprises at most 0.4% by weight nickel.

41. The alloy as claimed in claim 34, wherein the alloy comprises at least 350 ppm nitrogen.

42. The alloy as claimed in claim 34, wherein the alloy comprises at most 300 ppm nitrogen.

43. The alloy as claimed in claim 34, wherein the alloy comprises cobalt.

44. The alloy as claimed in claim 34, wherein the alloy comprises at least 0.9% by weight cobalt.

45. The alloy as claimed in claim 34, wherein the alloy comprises manganese.

46. The alloy as claimed in claim 34, wherein the alloy comprises no manganese.

47. The alloy as claimed in claim 34, wherein the alloy comprises silicon.

48. The alloy as claimed in claim 34, wherein the alloy comprises no silicon.

49. The alloy as claimed in claim 34, wherein the alloy comprises phosphorus.

50. The alloy as claimed in claim 34, wherein the alloy comprises no phosphorus.

51. The alloy as claimed in claim 34, wherein the alloy comprises sulfur.

52. The alloy as claimed in claim 34, wherein comprises no sulfur.

53. The alloy as claimed in claim 34, wherein the alloy contains no tungsten.