High-chromium heat-resistant steel

Abstract

The present invention provides a high-chromium heat-resistant steel. The steel contains in mass %, C: 0.08% to 0.13%; Si: 0.15% to 0.45%; Mn: 0.1% to 1.0%; Ni: 0.01% to 0.5%; Cr: 10.0% to 11.5%; Mo: 0.3% to 0.6%; V: 0.10% to 0.25%; Nb: 0.01% to 0.06%; N: 0.015% to 0.07%; B: ≤0.005%, and Al: ≤0.04%. The balance consists of Fe and inevitable impurity elements. The steel shows a martensitic microstructure.

Description

FIELD OF THE INVENTION

The present invention relates to a high-chromium heat-resistant steel.

BACKGROUND OF THE INVENTION

Until now, several 9% Cr heat-resistant steels containing delta ferrite have been proposed as high-chromium steels to improve weldability, and some of them have already been used for steam contacting components in thermal power plants. However, since 9% Cr heat-resistant steels are greatly impaired in long-term creep strength and impact properties, 9% Cr-1% Mo steels having martensitic microstructure not containing delta ferrite are mainly used now. In recent years, temperatures and pressures of steam conditions have been greatly increased to improve thermal efficiency in thermal power plants. Therefore, the operating conditions of power plants are changing from supercritical pressure to ultra supercritical pressure. In addition, plants operable under more severe steam conditions are planned. With such increasing severity in the steam conditions, the presently used 9% Cr-1% Mo steels (Grade 91 steels) cannot be adapted to boiler tubes in future plants because of their limited oxidation resistance and high temperature strength. Meanwhile, austenitic heat resisting stainless steels can be candidate materials to be used for future plants, but the application thereof is limited by economical efficiency. Hence, the development of heat-resistant steels is desired for the usage in steam conditions with even higher temperatures.

Under these circumstances, new types of high chromium steels primarily to improve the creep strength have been developed as disclosed in JP-A-1993-311342, JP-A-1993-311345 and JP-A-1997-291308. These steels have improved creep rupture strength and toughness by the addition of W as a solid-solution hardening element and, further, by the addition of alloy elements such as Co, Ni, and Cu. In addition, JP-A-1988-89644 discloses steels with optimized contents of W and Nb and improved creep strength. U.S. Pat. No. 4,564,392 describes Cr-containing steels in which the ratio of C/N is optimized. The steels exemplified in the latter US patent document contain relatively large amounts of Mo and N. Steel containing 12% Cr is considered particularly suitable for use at high temperatures and under high stress. All of these known steels allegedly have improved creep strength by the addition of alloy elements, such as W and Co to conventional heat-resistant steels through the solid-solution hardening. However, since W and Co are expensive elements leading to increase of material prices, the use of these elements is limited from the viewpoint of economical effects.

Further, the improvement of steam oxidation resistance is indispensable against high temperature steam. In addition, increasing the Cr content from the conventional 9% Cr steels is effective to improve the steam oxidation resistance in the existing condition. However, since increasing the Cr content results in the formation of delta ferrite, the austenite forming elements such as C and Ni are needed to be increased to obtain the tempered martensite structure. However, the contents of these elements are limited because the increase in C and Ni contents reduces the weldability and the long-term creep strength, respectively. Although there are cases where Co or the like is added to suppress the formation of delta ferrite, such an element is expensive, therefore resulting in decrease in the economical efficiency.

DISCLOSURE OF INVENTION

In view of the circumstances described above, an object of the present invention is to provide an improved high-chromium heat-resistant steel, consisting of in mass %, C: 0.08% to 0.13%; Si: 0.15% to 0.45%; Mn: 0.1% to 1.0%; Ni: 0.01% to 0.5%; Cr: 10.0% to 11.5%; Mo: 0.3% to 0.6%; V: 0.10% to 0.25%; Nb: 0.01% to 0.06%; N: 0.015% to 0.07%, B: ≤0.005%, and Al: ≤0.04%, wherein the balance is Fe and inevitable impurity elements. A further object is to provide steel capable of being used for ultra supercritical pressure boilers. A further object is to provide steel improved in creep rupture strength and in steam oxidation properties for high temperature steam under the base of economical steels without addition of expensive elements, such as W and Co.

The steel composition of the present invention comprises low carbon (C), manganese (Mn), silicon (Si), chromium (Cr), nickel (Ni), molybdenum (Mo), vanadium (V), niobium (Nb) and nitrogen (N).

In an embodiment, one or more of the following elements can be added: aluminum (Al) and Boron (B).

The remainder of the composition comprises iron (Fe) and inevitable impurities.

The present invention relates to a high-chromium heat-resistant steel. Embodiments thereof are shown in the following Table 1 (compositions are expressed in mass %), wherein the balance is Fe and inevitable impurity elements:

	TABLE 1
	Range (mass %)		Preferred Range
Legend	Element	Min	Max	Min	Max
M	C	0.08	0.13	0.08	0.11
M	Si	0.15	0.45	0.15	0.35
M	Mn	0.10	1.00	0.40	0.60
M	Ni	0.01	0.50	0.01	0.20
M	Cr	10.00	11.50	10.45	11.00
M	Mo	0.30	0.60	0.45	0.55
M	V	0.10	0.25	0.15	0.25
M	Nb	0.010	0.060	0.035	0.060
M	N	0.0150	0.0700	0.0400	0.0700
O	Al	—	0.040	—	0.025
O	B	0.001	0.005	0.002	0.004
I	P	—	0.030	—	0.018
I	S	—	0.010	—	0.005
I	Sn	—	0.0200	—	0.0200
I	Pb	—	0.0030	—	0.0030
I	As	—	0.0120	—	0.0120
I	Sb	—	0.0040	—	0.0040
I	Cu	—	0.25	—	0.25
I	Co	—	0.020	—	0.020
Legends:
M = Mandatory;
O = Optional;
I = Inevitable impurity element that may be present

In an embodiment of the high-chromium heat-resistant steel B is in the range of 0.001% to 0.005% by mass.

In an embodiment of the high-chromium heat-resistant steel, the mass % of the inevitable impurity elements is lower than 0.4%.

In an embodiment of the high-chromium heat-resistant steel, the inevitable impurity elements comprises elements other than: C, Si, Mn, Ni, Cr, Mo, V, Nb, N, Fe.

In an embodiment of the high-chromium heat-resistant steel, the inevitable impurities may comprise one or more of phosphorus (P), sulfur (S), cobalt (Co), copper (Cu), antimony (Sb), arsenic (As), tin (Sn) and lead (Pb).

In an embodiment of the high-chromium heat-resistant steel, P+S+Co+Cu+Sb+As+Sn+Pb≤0.40% (in mass %).

In an embodiment of the high-chromium heat-resistant steel, P+S+Co+Cu+Sb+As+Sn+Pb≤0.35% (in mass %).

The inevitable impurity elements relate to the normal contamination as result of the production of steel.

The present invention has provided a high-chromium heat-resistant steel with improved properties in both the creep rupture strength and steam oxidation resistance, which as hitherto been difficult in the conventional 9Cr-1Mo steel. In addition, the main composition of the present invention does not contain expensive elements such as W and Co and contain a smaller amount of Mo, therefore being advantageous in economical efficiency. Thus, the present invention can meet to the usage for future thermal power plants with higher temperature and pressure as steam conditions.

The invention further relates to a steam contacting component, e.g. a tube, made from a high-chromium heat-resistant steel according to the invention. The tube can be a seamless or welded tube.

The invention further relates to a pressure boiler comprising one or more steam contacting components, e.g. a boiler drum and/or a tube, made from a high-chromium heat-resistant steel according to the invention.

The invention further relates to a thermal power plant comprising a steam contacting component according to the invention.

The invention further relates to a thermal power plant comprising a pressure boiler according to the invention.

DETAILED DESCRIPTION FOR CARRYING OUT THE INVENTION

Reasons for limitations for the individual elements will be discussed below.

C: 0.08% to 0.13%;

C is an austenite forming element suppressing ferrite formation. Hence, an appropriate amount of C is determined with ferrite forming elements such as Cr, in order to obtain the tempered martensite structure. In addition, C precipitates as carbides of the MC type (M represents an alloying element (The same will applies hereinafter.)) and M₂₃C₆ type, which greatly affect the high temperature strength, and in particular, creep rupture strength. With C content of less than 0.08%, the amount of precipitation is insufficient for precipitation strengthening, and also the suppression of delta ferrite phase is imperfect. For this reason, the lower limit thereof is set to 0.08%. With the addition of more than 0.13% of C, weldability is impaired and toughness is decreased. Further, agglomerated coarsening of carbides is accelerated resulting in a decrease in the creep rupture strength on the high-temperature and long term side. For this reason, the range thereof is set to 0.08% to 0.13%, preferably within the range of 0.08% to 0.11% (mass percentage)

Si: 0.15% to 0.45%;

Si is added as a deoxidizing agent and for oxidation resistance. However, Si is a strong ferrite forming element and toughness is impaired by the ferrite phase. For this reason, the range thereof is set to 0.15% to 0.45% to balance the oxidation resistance and the tempered martensite structure; preferably within the range of 0.15% to 0.35% (mass percentage)

Mn: 0.1% to 1.0%;

Mn is added as a deoxidizing agent and a desulfurizing agent. In addition, it is also an austenite forming element suppressing the delta ferrite phase, but excessive addition thereof impairs the creep strength. For this reason, the range thereof is set to 0.1% to 1%; preferably within the range of 0.40% to 0.60% (mass percentage)

Ni: 0.01% to 0.5%;

Ni is a strong austenite forming element suppressing ferrite phase formation. However, excessive addition thereof impairs long-term creep rupture strength. For this reason, the range suggested is set from 0.01% to 0.5%, preferably within the range of 0.01% to 0.20% (mass percentage)

Cr: 10.0% to 11.5%;

Cr is an important element for securing steam oxidation resistance. Cr content of 10.0% or more is necessary from the viewpoint of steam oxidation resistance for high temperature steam. However, excessive addition of Cr as well as Si causes ferrite formation and also causes formation of brittle phases in long-term creep, thereby impairing the rupture strength. For this reason, the upper limit thereof is set to 11.5%, preferably within the range of 10.45% to 11% (mass percentage)

Mo: 0.3% to 0.6%;

Mo is a ferrite forming element while it increases the creep strength due to the effect of solid-solution hardening. However, excessive addition thereof results in the formation of delta ferrite and the precipitation of coarse intermetallic compounds not contributing to the creep rupture strength. For this reason, the range thereof is set to 0.3% to 0.6%, preferably within the range of 0.45% to 0.55% (mass percentage)

V: 0.10% to 0.25%;

V precipitates as fine carbonitrides and thereby improves both high temperature strength and creep rupture strength. With a content of less than 0.1%, the amount of precipitation is insufficient to increase the creep strength. In contrast, excessive addition thereof results in formation of bulky V (C, N) precipitates not contributing to the creep strength. For this reason, the range thereof is set to 0.1% to 0.25%, preferably within the range of 0.15% to 0.25% (mass percentage)

Nb: 0.01% to 0.06%;

Nb also precipitates as fine carbonitrides, and is an important element improving the creep rupture strength. A content of 0.01% or more is necessary to obtain this effect. However, similarly as V, excessive addition of Nb results in formation of bulky carbonitrides to reduce the creep rupture strength. Hence, the range thereof is set to 0.01% to 0.06%, preferably within the range of 0.035% to 0.06% (mass percentage)

N: 0.015% to 0.07%,

N precipitates as either nitrides or carbonitrides thereby to improve the creep rupture strength. It is also an austenite forming element to suppress delta ferrite phases. However, excessive addition thereof impairs toughness. For this reason, the range thereof is set to 0.015% to 0.070%, preferably within the range of 0.040% to 0.070% (mass percentage)

Al: ≤0.04%; and

Al can be used as a deoxidizing agent, but it impairs the long-term creep rupture strength with excessive addition. For this reason, when optionally used, the upper limit thereof is set to 0.04%, preferably less than 0.025% (mass percentage)

B: 0.001% to 0.005%.

B is an element strengthening the grain boundary and that has also the effect of the precipitation hardening as M₂₃(C,B)₆, thus being effective for improving the creep rupture strength. However, excessive addition thereof impairs workability under high temperatures leading to a cause of cracking, and also impairs the creep rupture ductility. For this reason, when optionally used, the range thereof is set to 0.001% to 0.005%, preferably from 0.002% to 0.004% (mass percentage).

P: ≤0.03%;

P is an Inevitable impurity element contained in melting raw materials and not easily reduced in steel making process. It impairs toughness at room temperatures and high temperatures as well as hot workability. If present, the upper limit is set to 0.03%, preferably lees than 0.018% (mass percentage)

S: ≤0.01%;

S is also an inevitable impurity element and it impairs hot workability. It also can be a cause of cracks, scratches, or the like. If present, the upper limit is set to 0.01%, preferably lees than 0.005% (mass percentage)

In the present invention, the manufacturing conditions are not specifically limited. The tempered martensite structure can be obtained by conventional normalizing treatment heated at temperatures in the range of 950 to 1150 degree centigrade followed by air cooling and tempering treatment heated at temperatures in the range of 700 to 800 degree centigrade.

EXAMPLES

Steels according to the present invention (Nos. A to C) and comparative steels (Nos. D to F) having chemical compositions shown in Table 2 were melted using a vacuum induction melting furnace, cast into 50 kg or 70 kg ingot, and then hot-rolled into steel plates with a thickness of 12 mm to 15 mm. Then, the steel plates were heat treated by normalizing and then tempering. The normalizing temperature is in a range of 1050° C. to 1100° C., and the tempering temperature is in a range of 770° C. to 780° C. Obtained microstructure is a tempered martensite structure, not containing delta ferrite. Among comparative steels, Steel D has a component system of 9Cr-1Mo steels called Grade 91 steels, which are widely used at present. Steel D was used as a steel representing existing materials.

TABLE 2
Division	Steel	C	Si	Mn	P	S	Ni	Cr	Mo	V	Nb	Al	N	B
Inventive steel	A	0.09	0.21	0.25	0.012	0.002	0.20	10.6	0.51	0.22	0.04	0.012	0.044	—
Inventive steel	B	0.12	0.42	0.75	0.009	0.003	0.15	10.3	0.55	0.18	0.05	0.008	0.028	—
Inventive steel	C	0.11	0.18	0.48	0.013	0.001	0.41	11.3	0.34	0.20	0.03	0.015	0.040	0.0025
Comparative	D	0.10	0.32	0.47	0.011	0.003	0.20	8.5	0.98	0.25	0.07	0.013	0.045	—
steel
Grade91
Comparative	E	0.13	0.29	0.53	0.015	0.004	0.17	12.2	0.48	0.21	0.03	0.007	0.048	—
steel
Comparative	F	0.09	0.36	0.38	0.009	0.002	0.31	9.2	0.38	0.16	0.04	0.019	0.035	—
steel

(mass %) The underlined figures indicate the value that is out of the range in the present invention.

Test specimens were taken from the heat treated plates and were subjected to creep rupture testing and steam oxidation testing. Creep rupture testing was performed using a 6 mm diameter specimen under testing temperature of 650° C. and stresses of 110 MPa and 70 MPa. For steels of this type, testing requires tens of thousands hours to clarify superiority or inferiority at testing temperature of 600° C., which is an actual temperature for real thermal power plants. Therefore, the testing temperature was elevated to 650° C., and two stress conditions were applied with estimated rupture time periods of about 1,000 hours and about 10,000 hours. Since the difference in the rupture time among steels is assumed to be small on a short-term side testing of about 1,000 hours using a 110 MPa testing condition, 70 MPa testing condition was applied as long-term testing of about 10,000 hours to differentiate the rupture strength among steels.

For steam oxidation testing, the temperature was set to 650° C., which is the same as that for the creep rupture testing. In the testing, an average thickness of scale formed on the surface of the specimen subjected to 1,000-hour steam oxidation testing was measured using an optical microscope. In this manner, the steam oxidation resistance was evaluated. The specimen is a small sample of 15 mm×20 mm×10 mm taken from the heat treated plate material.

The results of the creep rupture testing and the steam oxidation testing are shown in Table 3.

	TABLE 3
	Creep rupture time (h) Test	Steam oxidation
	temperature 650° C.	testing 650° C.,
		Stress:	Stress:	1000 h Average
Division	Steel	110 MPa	70 MPa	scale thickness (μm)
Inventive steel	A	883	25,451	39
Inventive steel	B	923	23,801	40
Inventive steel	C	783	21,985	33
Comparative	D	482	8,862	92
steel
Comparative	E	1,034	7,075	30
steel
Comparative	F	804	21,904	72
steel

Compared to the steel D equivalent to the existing Grade 91 steel, steels for the present invention demonstrate excellent high temperature properties. For example, the rupture time is three times or more in the long-term testing with the stress of 70 MPa and the average thickness of scale formed in steam oxidation is no more than half. Thus, significant improvements are shown in the creep rupture strength and the steam oxidation resistance.

Comparative steel E having higher Cr content of 12.2% significantly improves the steam oxidation resistance, however it decreases the long-term creep rupture strength. Although the microstructure of Steel E is tempered martensite, not containing delta ferrite, the decreased creep rupture strength is considered owing to an increase in Cr content. Comparative steel F having equivalent Cr content to the existing Grade 91 steels cannot improve the steam oxidation properties with considerably thick scales compared with steels of the present invention.

INDUSTRIAL APPLICABILITY

According to the present invention, it is possible to provide a high-chromium heat-resistant steel that enhances both the creep rupture strength and the steam oxidation resistance even not containing expensive elements such as W and Co and less containing Mo. Therefore the present invention provides excellent economical efficiency. The inventive steel can be advantageously used for steam contacting components, e.g. tubes for a pressure boiler and/or a boiler drum.

Claims

1. A high-chromium heat-resistant steel, consisting of, in mass %: C: 0.08% to 0.13%;Si: 0.15% to 0.45%;Mn: 0.1% to 1.0%;Ni: 0.01% to 0.5%;Cr: 10.0% to 11.5%;Mo: 0.3% to 0.6%;V: 0.15% to 0.25%;Nb: 0.01% to 0.06%;N: 0.015% to 0.07%,B: 0 to 0.005%; andAl: 0 to 0.04%;wherein the balance is Fe and inevitable impurity elements.

2. The high-chromium heat-resistant steel of claim 1, wherein B is in the range of 0.001% to 0.005% by mass.

3. The high-chromium heat-resistant steel of claim 1, wherein the mass % of the inevitable impurity elements is lower than 0.4%.

4. The high-chromium heat resistant steel of claim 1, consisting of, in mass %: C: 0.08% to 0.11%;Si: 0.15% to 0.35%;Mn: 0.40% to 0.60%;Ni: 0.01% to 0.2%;Cr: 10.45% to 11.0%;Mo: 0.45% to 0.55%;V: 0.15% to 0.25%;Nb: 0.035% to 0.06%;N: 0.040% to 0.070%;B: 0 to 0.005%; andAl: 0 to 0.04%;wherein the balance is Fe and inevitable impurity elements.

5. The high-chromium heat-resistant steel of claim 4, wherein B is in the range of 0.002% to 0.004%.

6. The high-chromium heat-resistant steel of claim 4, wherein Al: 0 to 0.025% by mass.

7. A steam contacting component made from the high-chromium heat-resistant steel of claim 1.

8. A pressure boiler comprising one or more steam contacting components made from the high-chromium heat-resistant steel of claim 1.

9. A thermal power plant comprising the steam contacting component of claim 7.

10. A thermal power plant comprising the pressure boiler of claim 8.

11. The steam contacting component of claim 7, wherein the steam contacting component is a tube.

12. The pressure boiler of claim 8, wherein the one or more steam contacting components is a boiler drum.

13. The pressure boiler of claim 8, wherein the one or more steam contacting components is a tube.

14. The high-chromium heat-resistant steel of claim 1, wherein the steel has a martensitic microstructure.

15. The high-chromium heat-resistant steel of claim 14, wherein the steel does not contain delta ferrite.

16. The high-chromium heat-resistant steel of claim 1, wherein the steel has a creep rupture time of at least 21,985 hours under a temperature of 650° C. and a stress of 70 MPa.

17. The high-chromium heat-resistant steel of claim 1, wherein the steel has a creep rupture time of at least 23,801 hours under a stress of 70 MPa at a temperature of 650° C.

18. The high-chromium heat-resistant steel of claim 1, wherein the steel has a creep rupture time of at least 25,451 hours under a stress of 70 MPa at a temperature of 650° C.

19. The high-chromium heat-resistant steel of claim 1, wherein the steel has a creep rupture time of between 21,985 and 25,451 hours under a stress of 70 MPa at a temperature of 650° C.

20. The high-chromium heat-resistant steel of claim 1, wherein the steel forms an average scale thickness of at most 33 μm under a steam oxidation temperature of 650° C. for 1000 hours.

21. The high-chromium heat-resistant steel of claim 1, wherein the steel forms an average scale thickness of at most 39 μm of under a steam oxidation temperature of 650° C. for 1000 hours.

22. The high-chromium heat-resistant steel of claim 1, wherein the steel forms an average scale thickness of at most 40 μm under a steam oxidation temperature of 650° C. for 1000 hours.

23. The high-chromium heat-resistant steel of claim 1, wherein the steel forms an average scale thickness of 33 to 40 μm under a steam oxidation temperature of 650° C. for 1000 hours.

24. The high-chromium heat-resistant steel of claim 1, wherein the steel has a creep rupture time of between 21,985 and 25,451 hours under a stress of 70 MPa at a temperature of 650° C., and wherein the steel forms an average scale thickness of 33 to 40 μm under a steam oxidation temperature of 650° C. for 1000 hours.

25. The high-chromium heat-resistant steel of claim 1, wherein Ni is in the range of 0.01% to 0.2% by mass.

26. The high-chromium heat-resistant steel of claim 1, wherein Mo is in the range of 0.45% to 0.6% by mass.