US20020020473A1

US20020020473A1 - Heat resistant high chromium ferritic steel

Info

Publication number: US20020020473A1
Application number: US09/754,050
Authority: US
Inventors: Yoshiatsu Sawaragi; Hiroyuki Senba
Original assignee: Individual
Current assignee: Nippon Steel Corp
Priority date: 1998-07-08
Filing date: 2001-01-05
Publication date: 2002-02-21
Also published as: JP3982069B2; DE69904336D1; JP2000026940A; DE69904336T2; EP1103626B1; WO2000003050A1; EP1103626A1; EP1103626A4

Abstract

A heat resistant high Cr ferritic steel comprising, in mass %, C : 0.02 to 0.15%, Mn: 0.05 to 1.5%, P : 0.03% or less, S : 0.015% or less, Cr: 8 to 13%, W : 1.5 to 4%, Co: 2 to 6%, V : 0.1 to 0.5%, Ta: 0.01 to 0.15%, Nb: 0.01 to 0.15%, Nd: 0.001 to 0.2%, N : 0.02% or less, B : 0.0005 to 0.02%, Al: 0.001 to 0.05%, Mo: 0 to 1%, Si: 0 to 1%, Ca: 0 to 0.02%, La: 0 to 0.2%, Ce: 0 to 0.2%, Y : 0 to 0.2%, Hf: 0 to 0.2%, the contents of Nd and N satisfying the formula: Nd(%) ≦5×N(%)+0.1(%), and the balance being Fe and incidental impurities. The steel is excellent in high temperature long term creep strength and toughness and can be used under the ultra super critical steam condition such as a temperature of 625° C. and a pressure of 300 atm.

Description

This application is a continuation of international application PCT/JP99/03231 filed on Jun. 16, 1999, the entire content of which is herein incorporated by reference.

BACKGROUND OF THE INVENTION

1. Field of the Invention

The present invention relates to a heat resistant high Cr ferritic steel, more particularly, a high Cr ferritic steel having excellent high temperature long term creep strength and toughness and being suitable for uses such as a heat resistant steel tube and pipe, a pressure vessel steel plate or a turbine steel member used under high temperature and high pressure conditions in a power boiler, in a nuclear power plant and in a chemical plant.

2. Description of the Related Arts

A heat resistant steel used under high temperature and high pressure condition such as those in a power boiler, a nuclear power plant and a chemical plant, is generally required to be excellent in high temperature strength, corrosion resistant property, oxidation resistant property and toughness.

An austenitic stainless steel such as JIS-SUS321H steel (Equivalent to AISI-TP321H), JIS-SUS347H steel (Equivalent to AISI-TP347H), a low alloy steel such as 2.1/4Cr-1Mo steel and a high Cr ferritic steel such as 9-12 Cr steel have been used in the past for these applications. Among them, a high Cr ferritic steel is superior to a low alloy steel in high temperature strength and corrosion resistant property at a temperature of 500 to 650° C. Furthermore, compared with an austenitic stainless steel, a high Cr ferritic steel has many advantages such that it is less expensive, high in thermal conductivity and excellent in thermal fatigue property because of low thermal expansion coefficient and also it does not cause stress corrosion cracking.

A steam condition of a power boiler has recently became higher and higher in temperature and pressure in order to improve a thermal efficiency further in a thermal power plant. An example of such steam condition is 538° C. in temperature and 246 atm in pressure, which is so-called a super critical condition. Furthermore, a steam condition such as 625° C. or higher in temperature and 300 atm or higher in pressure, so-called a ultra super critical condition, has been studied for a future operation. According to these changes in the steam condition, the properties required for a steel tube and pipe used in power boiler become severer. A ordinary high Cr ferritic steel, therefore, has faced the situation that it can not satisfy fully the requirement of a long term creep strength at a high temperature required for a higher steam condition.

An austenitic stainless steel has the properties which can satisfy the above-mentioned servere condition but it is expensive. Accordingly, many studies on an improvement of the properties of a high Cr ferritic steel has been carried out in order to utilize a high Cr ferritic steel which is less expensive compared with an austenitic stainless steel.

The inventors have already invented a heat resistant high Cr ferritic steel which is less expensive and excellent in creep strength and toughness when used for a long time under the ultra super critical condition with a high temperature and a high pressure. (Published Japan Patent Application No. 8-85850, No. 9-71845, No. 9-71846)

However, a further improvement of creep strength has been required in order to use a high Cr ferrite steel in a thermal power boiler operated under more severe steam condition such as the above-mentioned ultra super critical condition.

SUMMARY OF THE INVENTION

The object of this invention is to provide a heat resistant high Cr ferritic steel which is excellent in long term creep strength at a high temperature and toughness and can be used under the condition of high temperature and high pressure such as 625° C. or more and 300 atm or more.

The gist of the present invention is a heat resistant high Cr ferritic steel as described below.

A heat resistant high Cr ferritic steel having excellent high temperature long term creep strength and toughness, which comprises, by mass %,



C	0.02 to 0.15%	Mn	0.05 to 1.5%
P	0.03% or less	S	0.015% or less
Cr	8 to 13%	W	1.5 to 4%
Co	2 to 6%	V	0.1 to 0.5%
Ta	0.01 to 0.15%	Nb	0.01 to 0.15%
Nd	0.001 to 0.2%	N	less than 0.02%
B	0.0005 to 0.02%	Al	0.001 to 0.05%
Mo	0 to 1%	Si	0 to 1%
Ca	0 to 0.02%	La	0 to 0.2%
Ce	0 to 0.2%	Y	0 to 0.2%
Hf	0 to 0.2%,

the contents of Nd and N satisfying the following formula, and the balance being Fe and incidental impurities.

Nd(%)≦5×N(%)+0.1(%)

The inventors have studied in detail the effect of various alloy elements on high temperature long term creep strength and toughness of a heat resistant high Cr ferritic steel containing Nd, which was previously developed by the inventors, for its further improvement. As a result, the inventors have obtained the following findings and accomplished the present invention.

(a) Nd is effective in fixing an oxygen in a steel by forming Nd-oxides and thereby preventing a formation of oxides with some of Nd and V, which are the precipitation strengthening elements, and contribute to increase creep strength by precipitating fine carbides. Furthermore, Nd forms carbides such as NdC ₂. These carbides precipitate finely and stably even after used for a long period of time at a high temperature and therefore contribute greatly to increase high temperature long term creep strength. However, Nd has strong affinity with N (Nitrogen) and produces inclusions of coarse NdN in a steel containing a large amount of nitrogen. Accordingly, in such steel, the effects of Nd in preventing a formation of oxides of Nb and V and in precipitating fine carbides such as NdC₂for a precipitation strengthening become insufficient and Nd can not fully attain its effect in improving creep strength.

(b) A formation of coarse NdN can be prevented by controlling an amount of N to be less than 0.02% in a heat resistant high Cr ferritic steel containing Nd. As a result, fine carbides of Nb and V and fine carbides such as NdC ₂precipitate stably, even after exposed for a long time at a high temperature, and thereby a recovery and softening phenomena of a martensite structure is suppressed even after being used for a long time at a high temperature, which result in great improvement of creep strength.

(c) In order to ensure toughness of a heat resistant high Cr ferritic steel containing Nd, the balance of the amounts of Nd and N is important and must satisfy the formula mentioned above.

DETAILED DESCRIPTION OF THE INVENTION

The following are the reasons why the chemical composition of the heat resistant steel of the present invention is regulated. (hereinafter, the % represents a mass percent)

C: 0.02 to 0.15%

C forms MC type carbides (M represents an alloying element), such as M ₇C₃and M₂₃C₆type carbides. These carbides contribute to increase creep strength and also C itself stabilizes a metallurgical structurebyservingasanaustenite-stabilizingelement. However, when the C content is less than 0.02%, the precipitation of carbides is insufficient and the amount of δ-ferrite increases, which results in the failure to obtain the satisfactory creep strength and toughness. However, when C is contained excessively in an amount of more than 0.15%, a coarsening of carbides occurs from the early stage of service, thereby resulting in lowering long term creep strength and impairing formability and weldability. Therefore, the upper limit of the C content is set to 0.15%. As a result, the C content is preferably set to 0.05 to 0.13%.

Mn: 0.05 to 1.5%

Mn is an element effective in serving as a deoxidizer and fixing S, and also serves as an austenite-stabilizing element. In order to obtain these effects, the Mn content must be 0.05% or more. However, the Mn content exceeding 1.5% deteriorates tougness of the steel. Therefore the Mn content is set to 0.05 to 1.5%, preferably 0.05 to 0.7%.

P: 0.03% or less S: 0.015% or less

P and S, which are impurity elements, are detrimental to hot workability, weldability and toughness. Therefore, it is preferable that the P and S contents are as low as possible but the P content of 0.03% or less and the S content of 0.015% or less do not directly affect the properties of the steel of this invention. Accordingly, the upper limits of P and S contents are set to 0.03% and 0.015%, respectively.

Cr: 8 to 13%

Cr is an essential element for the steel of this invention to ensure corrosion resistance and oxidation resistance, particularly steam oxidation resistance, at a high temperature. Besides, Cr forms carbides and thereby increases creep strength. Cr also forms tight oxide-film to thereby improve corrosion resistance and oxidation resistance. In order to obtain these effects, the Cr content must be 8% or more. However, an excessive Cr content promotes the formation of δ-ferrite to thereby deteriorate toughness of the steel. Therefore, the upper limit of Cr content is set to 13%. The Cr content is preferably set to 9 to 12%.

W: 1.5 to 4%

W is one of the main elements serving as a strengthening element of the steel of this invention. W precipitates finely and dispersively in a form of inter-metallic compounds such as the Fe ₇W₆type μ-phase and the Fe₂W type Laves phase during high temperature service, thereby contributing to the improvement of long term creep strength. Furthermore, W is also dissolved partially into Cr-carbides and prevents the carbides from gathering and coarsening, thereby contributing to maintaining strength of the steel. However, an excessive amount of W promotes the formation of δ-ferrite. Therefore, the W content is set to 1.5 to 4%, preferably 2 to 3.5%.

Co: 2 to 6%

Co is an austenite-stabilizing element and essential for the steel of this invention into which W is intentionally added. Co does not impair creep strength and rather increase creep strength. In this respect, Co differs from Ni which is also an austenite-stabilizing element. In order to attain these effects, Co must be added in an amount of 2% or more but an excessive Co content exceeding 6% lowers remarkably Ac ₁, transformation temperature of the steel and impairs creep strength of the steel. Therefore, the Co content is preferably set to 2 to 4%.

V: 0.1 to 0.5%

V is an important element for the steel of this invention in order to form the fine carbonitrides, thereby contributing to the improvement of creep strength. In order to obtain this effect, the V content must be 0.1% or more, but the effect saturates when the V content is more than 0.5%. Therefore, the V content is set to 0.1 to 0.5%, preferably 0.15 to 0.35%.

Ta: 0.01 to 0.15% Nb: 0.01 to 0.15%

Ta and Nb, as well as V, f orm the f ine carbonitrides, contributing to the improvement of creep strength. In order to obtain this effect, each of the contents of Ta and Nb must be 0. 01% or more, respectively, but the ef fect saturates when each content is more than 0. 15%. Therefore, each of the contents of Ta and Nb is set to 0.01 to 0.15%, preferably 0.01 to 0.1%.

Nd: 0.001 to 0.2%

Nd is ef fective to precipitate the carbides such as NdC ₂finely and stably even after used for a long term at a high temperature, thereby contributing greatly to prevent the recovery and sof tening of a martensite structure and to increase creep strength. In order to obtain these effects, the Nd content must be 0.001% or more but an excessive Nd content exceeding 0.2% deteriorates toughness of the steel. Therefore, the Nd content is set to 0.001 to 0.2%, preferably 0.005 to 0.15%.

N: less than 0.02%

N, as well as C, serves as an austenite-stabilizing element. However, in the steel containing Nd, when an amount of N increases, a coarse NdN remains as an inclusion in the steel, thereby impairing the improvement effect of creep strength by Nd and also toughness of the steel. Therefore, in order to secure the effect of Nd fully, the upper limit of the N content in the steel must be less than 0.02%. When toughness of the steel is particularly important, it is preferable that the balance of the Nd content and the N content is controlled to satisfy the following formula. The N content is preferably not more than 0.017%

Nd(%)≦5×N(%)+0.1(%)

B: 0.0005 to 0.02%

B has an effect of precipitating the M ₂₃C₆type carbide finely and dispersively when B is added in a small amount. Thus, B contributes to the improvement of the high temperature long term creep strength. B is also effective in increasing the quench-hardening property, especially for a steel product having a heavy wall whose cooling speed after a heat-treatment is slow, thereby attaining an important role in securing high temperature strength. This effect becomes remarkable when the B content is 0.0005% or more, but the B content exceeding 0.02% forms the coarse precipitations, thereby lowering toughness of the steel. Therefore, the B content is set to 0.0005 to 0.02%, preferably 0.002 to 0.01%.

Al: 0.001 to 0.05%

Al must be contained in an amount of 0.001% or more for serving as a deoxidizer in the molten steel. However, an excessive Al content exceeding 0.05% lowers creep strength. Therefore, the Al content is set to 0.001 to 0.05%, preferably 0.001 to 0.03%.

Si: 0 to 1%

Si is optionally added to serve as a deoxidizer in the molten steel. Si is effective to increase steam oxidation resistance at a high temperature. However, since an excessive Si content exceeding 1% deteriorates toughness of the steel, the Si content is set to 0 to 1%. When steam oxidation resistance is particularly important, it is preferable that the Si content is 0.1% or more.

Mo: 0 to 1%

Mo is an optional element which contributes to the improvement of creep strength by serving as a solution strengthening element. However, the Mo content exceeding 1% accelerates to precipitate an inter-metallic compound such as the Laves phase. In the steel containing Mo, the inter-metallic compound precipitates very coarsely, which thereby does not contribute to the improvement of creep strength and also lowers toughness of the steel after aging. Therefore, the Mo content is set to 0 to 1%.



Ca	0 to 0.02%	La	0 to 0.2%	Ce	0 to 0.2%
Y	0 to 0.2%	Hf	0 to 0.2%

At least one element selected from Ca, La, Ce, Y and Hf is optionally added. These elements are effective in improving creep strength and also hot workability of the steel by strengthening the grain boundaries even if the amount of the addition is very little. However, excessive amount of these elements deteriorates hot workability of the steel. Therefore, the upper limit of the Ca content is set to 0.02% and each of the upper limits of La, Ce, Y and Hf is set to 0.2%, respectively.

Examples [0049]
The present invention will next be described in detail by way of various examples but these examples should not be construed as limiting the invention. [0050]

The steels having the chemical composition shown in Table 1 and Table 2 were melted in a vacuum induction furnace and cast into the 50 Kg ingots with a diameter of 144 mm. In the tables, the steel No.1 to No.23 are the examples of the steel of this invention and the steel A to Q are the comparative examples.

TABLE 1


(Balance: Fe, mass %)

Nd-5N-

Steel

0.10

No.

C

Si

Mn

P

S

Cr

Co

W

Mo

Nd

V

Ta

Nb

N

B

Al

others

value

1	0.082	0.18	0.20	0.015	0.003	10.95	2.90	3.05	—	0.05	0.20	0.05	0.06	0.005	0.0025	0.008		−0.065
2	0.830	0.17	0.18	0.015	0.003	10.90	2.87	3.07	—	0.05	0.21	0.05	0.05	0.012	0.0027	0.006		−0.110
3	0.079	0.16	0.22	0.016	0.003	10.98	2.93	3.10	—	0.05	0.21	0.06	0.06	0.018	0.0025	0.006		−0.140
A	0.080	0.18	0.25	0.015	0.002	10.90	2.90	3.05	—	0.05	0.21	0.05	0.06	0.045*	0.0030	0.007		−0.275
4	0.091	0.25	0.23	0.017	0.003	10.45	2.33	2.85	—	0.10	0.19	0.05	0.06	0.004	0.0045	0.005		−0.020
5	0.093	0.25	0.26	0.016	0.002	10.40	2.36	2.86	—	0.11	0.21	0.05	0.05	0.012	0.0043	0.006		−0.050
6	0.090	0.23	0.24	0.015	0.002	10.45	2.30	2.90	—	0.12	0.20	0.06	0.06	0.017	0.0040	0.006		−0.065
B	0.093	0.26	0.25	0.016	0.001	10.48	2.35	2.90	—	0.12	0.20	0.05	0.06	0.043*	0.0042	0.005		−0.195
7	0.102	0.35	0.45	0.013	0.001	10.85	3.50	3.25	—	0.18	0.17	0.08	0.06	0.010	0.0028	0.010		0.030
C	0.103	0.37	0.48	0.013	0.001	10.80	3.52	3.27	—	0.18	0.17	0.08	0.05	0.038*	0.0027	0.008		−0.110
8	0.100	0.23	0.25	0.015	0.001	10.40	3.50	2.52	0.15	0.05	0.22	0.05	0.06	0.013	0.0038	0.010		−0.115
D	0.098	0.23	0.24	0.014	0.001	10.35	3.52	2.54	0.17	0.05	0.21	0.05	0.06	0.043*	0.0040	0.008		−0.265
9	0.050	0.11	0.27	0.018	0.003	8.63	2.30	1.75	—	0.08	0.15	0.05	0.06	0.015	0.0018	0.007		−0.095
E	0.053	0.10	0.24	0.019	0.003	8.58	2.32	1.79	—	0.08	0.15	0.05	0.06	0.055*	0.0018	0.006		−0.295
10	0.135	0.55	0.27	0.013	0.001	12.13	5.38	3.50	—	0.08	0.22	0.10	0.07	0.007	0.0070	0.013		−0.055
F	0.137	0.57	0.24	0.010	0.001	12.15	5.36	3.55	—	0.08	0.21	0.11	0.07	0.042*	0.0073	0.015		−0.230
11	0.090	0.26	1.35	0.013	0.002	10.85	3.20	3.03	—	0.05	0.22	0.02	0.05	0.007	0.0030	0.010		−0.085
G	0.088	0.26	1.38	0.010	0.001	10.90	3.16	3.05	—	0.04	0.23	0.02	0.06	0.028*	0.0033	0.009		−0.200
12	0.090	0.26	0.35	0.013	0.001	10.45	3.25	3.15	—	0.05	0.22	0.05	0.06	0.010	0.0028	0.008	Ca:0.0045	−0.100
H	0.093	0.23	0.32	0.015	0.001	10.35	3.28	3.10	—	0.05	0.22	0.06	0.06	0.045*	0.0030	0.011	Ca:0.0048	−0.275

TABLE 2


(Balance: Fe, mass %)

Nd-5N-

Steel

0.10

No.

C

Si

Mn

P

S

Cr

Co

W

Mo

Nd

V

Ta

Nb

N

B

Al

others

value

13	0.078	0.20	0.35	0.017	0.003	10.30	3.02	2.86	—	0.10	0.20	0.10	0.05	0.006	0.0052	0.004	La:0.050	−0.030
I	0.081	0.19	0.35	0.016	0.003	10.32	3.05	2.83	—	0.11	0.20	0.09	0.06	0.054*	0.0053	0.006	La:0.053	−0.260
14	0.105	0.28	0.37	0.012	0.002	10.78	3.26	3.12	—	0.07	0.22	0.03	0.05	0.008	0.0042	0.014	Ce:0.034	−0.070
J	0.105	0.26	0.40	0.012	0.001	10.73	3.34	3.12	—	0.08	0.20	0.02	0.06	0.038*	0.0043	0.012	Ce:0.036	−0.210
15	0.110	0.20	0.23	0.015	0.001	10.23	3.13	3.50	—	0.07	0.18	0.05	0.07	0.013	0.0040	0.011	Y:0.017	−0.095
K	0.113	0.19	0.20	0.013	0.001	10.20	3.17	3.62	—	0.08	0.19	0.04	0.07	0.058*	0.0044	0.008	Y:0.020	−0.310
16	0.090	0.20	0.25	0.010	0.001	9.80	2.98	2.87	—	0.09	0.25	0.07	0.05	0.010	0.0022	0.004	Hf:0.025	−0.060
L	0.093	0.20	0.28	0.010	0.001	9.78	2.95	2.83	—	0.09	0.24	0.07	0.04	0.046*	0.0020	0.006	Hf:0.028	−0.240
17	0.097	0.28	0.46	0.015	0.001	10.60	3.26	3.03	—	0.11	0.22	0.05	0.06	0.006	0.0032	0.007		−0.020
18	0.100	0.29	0.45	0.015	0.001	10.55	3.28	3.08	—	0.18	0.21	0.04	0.06	0.006	0.0032	0.009		0.050
19	0.088	0.25	0.40	0.014	0.001	10.85	2.75	2.53	—	0.15	0.20	0.03	0.06	0.014	0.0054	0.013		−0.020
20	0.091	0.26	0.44	0.016	0.001	10.81	2.70	2.47	—	0.19	0.20	0.03	0.06	0.014	0.0056	0.014		0.020
21	0.078	0.38	0.34	0.013	0.001	10.38	3.10	1.80	0.45	0.13	0.24	0.07	0.07	0.010	0.0032	0.027		−0.020
22	0.080	0.40	0.43	0.015	0.001	10.41	3.14	1.76	0.43	0.17	0.24	0.07	0.06	0.010	0.0032	0.029		0.020
23	0.062	0.25	0.41	0.008	0.001	10.12	5.23	3.78	—	0.10	0.22	0.10	0.05	0.004	0.0010	0.005	Ca:0.0075,	−0.020
																	Y:0.0087	−0.020
24	0.065	0.26	0.36	0.009	0.001	10.10	5.20	3.78	—	0.15	0.23	0.11	0.07	0.004	0.0009	0.007	Ca:0.0073,	0.030
																	Y:0.0090

These steel ingots were hot-forged and then hot-rolled to the steel plates with a thickness of 20 mm. The steel plates were heated at 1050° C. for 1 hour and then air-cooled. After that, the steel plates were heated for a temper treatment at 780 ° C. for 1 hour and air-cooled. The creep rupture test specimens and the Charpy impact test specimens were prepared from the thus-obtained steel plates and the creep rupture tests and the Charpy impact tests were carried out under the following conditions. [0053]
(1) Creep rupture test [0054]
Specimen: Diameter 6.0 mm, Gage length 30 mm [0055]
Test temperature: 650° C. [0056]
Applied stress: 98 MPa [0057]
(2) Chary impact test [0058]
Specimen: 10mm×10mm×55mm, 2mm V-notch [0059]
Test temperature: 0° C. [0060]

The creep rupture time and the Charpy impact value(J/cm ²) obtained by the above-mentioned tests are shown in Table 3 and Table 4.

TABLE 3


(Examples of the present invention)

	Creep rupture time
Steel	650° C. × 98 MPa	Charpy impact value*
No.	(hrs)	at 0° C. (J/cm²)

1	18789.5	186
2	18502.3	190
3	17462.0	196
4	19711.2	178
5	19465.7	170
6	19396.0	175
7	20035.3	150
8	17690.0	185
9	16683.7	205
0	21475.5	160
1	17180.3	178
2	19334.0	195
3	18863.7	202
4	20181.5	195
5	22430.0	170
6	20003.7	175
7	19499.0	183
8	19023.0	150
9	18753.7	178
0	18552.5	148
1	17263.5	195
2	17022.0	165
3	23176.3	170
4	23105.3	150

TABLE 4


(Comparative examples)

	Creep rupture time
Steel	650° C. × 98 MPa	Charpy impact value*
No.	(hrs)	at 0° C. (J/cm²)

A	15172.0	180
B	16123.5	170
C	16547.7	143
D	15120.3	183
E	13489.3	200
F	16362.0	150
G	13896.7	175
H	16501.3	187
I	15141.4	195
J	15859.7	187
K	16724.0	165
L	15879.5	173

It can be found that the creep rupture times of the steel No.1 to 3 and No.4 to 6, which are the examples of this invention containing N of less than 0.02%, are significantly improved in comparison with the steels A and B, which are the comparative examples containing N exceeding the amount defined by this invention. The effect of the improvement in creep rupture life by reducing the N content is obvious in the steels No.7 to 17, which are the examples of this invention, when they are compared with the steels C to M, which are the comparative examples corresponding to the steels No.7 to 17, respectively. [0063]
In the steels N,O,P and Q, which are the comparative examples, the contents of Nd and N do not satisfy the following formula. In this case, comparing with the steels No.17, 19, 21 and 23, which are the examples of this invention and satisfy the following formula, it can be found that there is almost no difference in creep rupture life, but the impact value is lower. Therefore, when toughness of the steel is important, it is preferable to control the contents of Nd and N within the range satisfying the following formula. [0064]
Nd(%)≦5×N(%)+0.1(%)
Industrial Applicability [0065]
The heat resistant high Cr ferritic steel according to the present invention is excellent in high temperature long term creep strength at a high temperature of 625° C. or more and in toughness at room temperature and thus can achieve superior performance as a material for a heat resistant steel tube and pipe, a pressure vessel steel plate and a turbine steel member used in a field of a nuclear power plant and a chemical plant. Therefore, this steel has a great advantage for an industrial application. [0066]

Claims

What is claimed is:

1. A heat resistant high Cr ferritic steel excellent in high temperature long term creep strength and toughness, which comprises, in mass %,

Nd(%)≦5×N(%)+0.1(%)

2. A ferritic steel according to claim 1, wherein the W content is 2 to 3.5%.

3. A ferritic steel according to claim 1, wherein the V content is 0.15 to 0.35% and the Nd content is 0.005 to 0.15%.

4. A ferritic steel according to claim 2, wherein the V content is 0.15 to 0.35% and the Nd content is 0.005 to 0.15%.