EP2692887B1

EP2692887B1 - Cast austenitic stainless steel

Info

Publication number: EP2692887B1
Application number: EP12765111.5A
Authority: EP
Inventors: Nobuyuki Sakamoto; Makoto Hineno
Original assignee: Kubota Corp
Current assignee: Kubota Corp
Priority date: 2011-03-31
Filing date: 2012-02-24
Publication date: 2017-07-19
Anticipated expiration: 2032-02-24
Also published as: JP5863770B2; JPWO2012132679A1; WO2012132679A1; CN103429778B; EP2692887A4; US20140056751A1; CA2830586A1; CN103429778A; EP2692887A1; KR20140044318A

Description

Technical Field

The present invention relates to an austenitic stainless cast steel.

Background Art

An austenitic stainless cast steel exhibits excellent properties especially in corrosion resistance, strength, weldability and the like, and has been widely used for piping, valves and the like in chemical plants and power plants. The austenitic stainless cast steel is formed of, for example from metallurgical viewpoint, two phases including approximately 10 - 20% of an alpha phase and approximately 90 - 80% of a gamma phase (austenitic phase).
As for steel castings of the austenitic stainless steel, CF8C has been known. For example, a CF8C austenitic stainless steel casting includes: up to 0.08 percent by mass of C (carbon); up to 2.0 percent by mass of Si (silicon); up to 1.5 percent by mass of Mn (manganese); 18.0 - 21.0 percent by mass of Cr (chromium); 9.0 - 12.0 percent by mass of Ni (nickel); and up to 1.0 percent by mass of Nb (niobium).
CF8C includes approximately 12.0% of a ferrite phase. The ferrite phase can be, for example, measured as ferrite content in the austenitic stainless steel with a known ferrite scope, or calculated using a Schaeffler diagram based on component elements, and is indicated with volume fraction (percent (%)).
The ferrite phase is considered effective for preventing weld cracking and reducing stress corrosion cracking. However, if a ferrite phase content is large, for example, exposure of CF8C to high temperature for a long period of time may transform the ferrite phase into a sigma phase (σ phase), which is a compound of iron and chromium. This may lead to embrittlement of the steel casting.
Patent Document 1 discloses CF8C-Plus, which is an alloy modified from CF8C, and describes that CF8C-Plus does not contain ferrite phase. Patent Document 1 also describes that CF8C-Plus includes: 0.05 - 0.15 percent by mass of C; 0.2 - 1.0 percent by mass of Si; 0.5 - 10.0 percent by mass of Mn; 18.0 - 25.0 percent by mass of Cr; 10.0 - 15.0 percent by mass of Ni; 0.1 - 1.5 percent by mass of Nb; and 0.05 - 0.5 percent by mass of N.
In Patent Document 1, an absence of the ferrite phase from CF8C-Plus is considered important for retaining the properties imparted at casting of materials during a life of the component part produced from the materials.
When CF8C is exposed to high temperature for a long period of time under usage environment, the sigma phase is precipitated to cause aging embrittlement, and thus aging ductility may become poor. Also in the case of CF8C-Plus described in Patent Document 1, further improvement has been demanded in oxidation resistance.
Therefore, it has been desired to provide an austenitic stainless cast steel exhibiting excellent aging ductility and oxidation resistance.
The Japanese patent application JP H02-97648 A discloses an austenitic stainless steel having a composition consisting of, by weight, ≤ 0.03 % C, ≤ 2 % Si, ≤ 10% Mn, 6 to 20 % Ni, 16 to 30 % Cr, 0.1 to 0.3 % N, 0.02 to 0.25 % Nb, and the balance Fe is refined. This steel is rough rolled at 1000 to 1200 °C and ≥ 50 % draft. After the above roughing, the steel is cooled for 10 sec to 5 minutes subsequently, the steel is rolled at 800 to 1000 °C finish rolling temperature and ≥ 30% draft and then cooled at ≥ 4 °C/min cooling rate, by which the structure of the steel is formed into recrystallization working duplex structure.
Shim J. H. et al. refers to numerical simulations of long-term precipitate evolution in austenitic heat-resistant steels being published in Calphad Computer Coupling of Phase Diagrams and Thermochemistry, New York, vol. 34, no. 1, March 1, 2010 pages 105 to 112, ISSN 0364-5916.
The Japanese patent application JP H02-97647 A discloses a steel constituted of, by weight, ≤ 0.03 % C, ≤ 20 % Si, ≤ 10 % Mn, 6 to 20 % Ni, 16 to 30 % Cr, 0.1 to 0.3 % N, 0.02 to 0.25 % Nb and the balance Fe is melted. The steel is rolled at 1000 to 1200 °C rough rolling temperature at ≥ 50% working ratio and it is thereafter cooled for 16 sec to 5 minutes. The steel is then rolled at 800 to 1000 °C finish rolling temperature at ≥ 30 % working ratio and is thereafter cooled at ≥ 4 °C/min cooling speed to form its structure into the recrystallization treated double constitutional one.
The Japanese patent application JP S63-169362 A discloses a nonmagnetic steel consisting of, by weight, ≤ 0.15 % C, ≤ 1.0 % Si, ≤ 5.0 % Mn, ≤ 0.030 % S and the balance Fe with inevitable impurities. It contains 7.0 to 15.0 % Ni, 16.0 to 22.0 % Cr, ≤ 0.5 % Nb and 0.1 to 0.4 % N and it further contains ≤ 7.5 % in total of one or more among ≤ 4.0 % Mo, ≤ 3.0 % Cu and ≤ 0.5 % V and/or ≤ 0.31 % in total of one or more among ≤ 0.20 % rare earth element, ≤ 0.10 % Ca, ≤ 0.10 % Mg and ≤ 0.01 %.
The Japanese patent application JP S63-53244 A discloses a stainless steel consisting of, by weight, ≤ 0.03 % C, ≤ 2 % Si, ≤ 5 % Mn, 6 to 13 % Ni, 16 to 21 % Cr, 0.1 to 0.3 % N, 0.02 to 0.25 % Nb, and the balance Fe is refined. This steel is rolled at 1,000 to 1,200 °C at ≥ 50% draft and cooled for 10sec to 5min, which is subjected to finish rolling at 800 to 1,000 °C at ≥ 30 % draft and then to cooling at a cooling rate of ≥ 4 °C/min.
The Japanese patent application JP S60-121098 A discloses a build-up weld layer of an austenitic stainless steel having a composition containing ≤ 0.1 % C, ≤ 1.0 % Si, ≤ 3.0 % Mn, 17.0 t 23.0 % Cr, 7.0 to 15.0 % Ni, ≤ 0.4 % Mo and ≤ 1.0 % Nb and consisting of 0.08 to 0.20 % N. The calculated value of the delta ferrite by the prescribed formula is kept within a -2.0 to 20.0 % range.
The German patent application DE 26 34 403 A1 discloses a stainless cast alloy steel suitable for ground joint portions, airtight portions, sliding portions, etc., used at low temperatures. This steel comprises from about 0.03 to about 0.15 % by weight of C; up to about 2 % by weight of Si; up to about 2 % by weight of Mn; from about 18 to about 26 % by weight of Cr; from about 5 to about 13 % by weight of Ni, the remainder being Fe and unavoidable trace impurities; wherein a ferrite phase is present in an amount of from about 10 to about 40 % by volume, based on the volume of the stainless cast alloy steel.

Citation List

Patent Literature

Patent Document 1: Japanese translation of a PCT application Kohyo No. 2009-545675

Summary of Invention

In order to provide such an austenitic stainless cast steel, the inventions of the following items (1) - (5) are provided.

(1) An austenitic stainless cast steel, wherein a volume fraction of the ferrite phase is 0.1 - 5.0 %, and the cast steel consists of: 0.01 - 0.10 percent by mass of C; 0.6 - 1.0 percent by mass of Si; 2.0 - 2.8 percent by mass of Mn; 0.1 - 0.4 percent by mass of N; 18.0 - 24.0 percent by mass of Cr; 8.0 - 15.0 percent by mass of Ni; 0.2 - 0.7 percent by mass of Nb; and the balance is Fe and inevitable impurities.
(2) The austenitic stainless cast steel according to item (1), wherein the volume fraction of the ferrite phase is 0.5 - 3.0.
(3) The austenitic stainless cast steel according to item (1) or (2), wherein Mn is 2.07 - 2.8 percent by mass and Nb is 0.26 - 0.7 percent by mass.
(4) A method of producing the austenitic stainless cast steel according to any one of items (1) - (3), the method comprising: a melting of metal components in a melting furnace, and a cooling of the molten metal componensts from a temperature range of 1,150 - 1,350 °C to a temperature range of 600 - 800 °C at a cooling rate of 30 °C/min or more.
(5) A valve formed of austenitic stainless cast steel according to any one of items (1) - (3).

The austenitic stainless cast steel of the present invention is excellent in, for example, aging ductility, tensile strength and oxidation resistance, as will be described in Examples. Especially, the aging ductility in Examples of the present invention was approximately 2.4 times as high as that in Comparative Examples. Likewise, oxidation resistance in Examples of the present invention was approximately 9.5 times as high as that in Comparative Examples.
The reason that the austenitic stainless cast steel exhibits such excellent properties seems to be that the volume fraction of the ferrite phase is 0.1 - 5.0 %, and the contents of the components C, Si, Mn, Cr, Ni, Nb and N seem to play important roles. Hereinbelow, each component will be described in detail.
By setting the volume fraction of the ferrite phase to 0.1 - 5.0 %, even when the cast steel is exposed to high temperature for a long period of time, a precipitation amount of the sigma phase can be suppressed low. Since the precipitation amount of the sigma phase is low, the austenitic stainless cast steel is unlikely to be embrittled, and exhibits excellent aging ductility.
C has an effect of lowering a melting point and improving fluidity, i.e. castability of molten metal. In addition, it is preferable that the amount of C is low from the viewpoint of corrosion resistance, and if a large amount is added, the corrosion resistance of the base metal is reduced. In view of these, in order to improve high-temperature ductility, an additive amount of C in the present invention is set to 0.01 - 0.10 percent by mass.
Si serves as deoxidizing agent for molten metal, and is effective for improving fluidity, oxidation resistance, and weldability. However, an excessive addition will make the austenitic structure unstable, leading to deterioration of castability, hinder workability and weldability, and promotion of weld cracking. Therefore, an additive amount of Si in the present invention is set to 0.6 - 1.0 percent by mass.
Mn is effective as deoxidizing agent for molten metal, and enhances fluidity during the casting to thereby improve productivity. In addition, it is also effective for reducing weld cracking. Since an excessive addition will deteriorate oxidation resistance, an additive amount of Mn in the present invention is set to 2.0 - 2.8 percent by mass. When Mn is in this range, the austenitic stainless cast steel exhibiting excellent oxidation resistance can be obtained, as will be described in Examples.
N improves high-temperature strength and thermal fatigue resistance, and is a strong austenite forming element which stabilizes an austenitic matrix. In addition, N is an element effective for grain refining. With this grain refining, ductility of the material which is important as structure can be secured, and in addition, a drawback of poor machinability, which is specific in the austenitic stainless cast steel, can be improved. Especially, N renders excellent perforation machinability to a member to be perforated for connecting parts. When N is added in a large amount, embrittlement is promoted, while an effective Cr amount is reduced and thus oxidation resistance is deteriorated. Therefore, an additive amount ofN in the present invention is set to 0.1 - 0.4 percent by mass.
Cr improves oxidation resistance and stabilizes the ferrite structure. In order to reliably attain this effect, the amount of Cr is set to 18.0 percent by mass or more. On the other hand, an excessive addition will lower the aging ductility of the steel due to excessive precipitation of Cr carbide when the cast steel is used at high temperature, and thus the upper limit of the Cr amount is set to 24.0 percent by mass.
Ni facilitates the formation of the stable austenitic matrix, stabilizes the austenitic phase, and enhances high-temperature strength and oxidation resistance of the steel. Taking excellent castability, corrosion resistance and weldability into consideration, an additive amount of Ni in the present invention is set to 8.0 - 15.0 percent by mass.
Nb binds with C to form fine carbide, and improves high-temperature strength. In addition, the formation of Cr carbide is suppressed, and thus oxidation resistance can be improved. In order to effectively exert these effects, the content of 0.2 % or more is required. However, when Nb is added in an excessive amount, heat cracking susceptibility is notably enhanced, and inner quality will be deteriorated. Therefore, an additive amount of Nb in the present invention is set to 0.2 - 0.7 percent by mass.
In addition, the austenitic stainless cast steel of the present invention can be produced by performing cooling from a temperature range of 1,150 - 1,350°C to a temperature range of 600 - 800°C at a cooling rate of 30°C/min or more. By producing the austenitic stainless cast steel of the present invention under the above-described conditions, excellent strength property can be obtained, and thus solution heat treatment can be omitted.
The produced austenitic stainless cast steel is used as, for example, materials for piping, valves and the like in chemical plants and power plants.

Brief Description of Drawings

Fig. 1 is a graph showing results of oxidation resistance (mm/year) examined with respect to the austenitic stainless cast steel.

Description of Embodiments

Hereinbelow, embodiments of the present invention will be described with reference to the drawings.
The austenitic stainless cast steel of the present invention is formed in such a manner that the volume fraction of the ferrite phase becomes 0.1 - 5.0%, preferably 0.5 - 3.0%. The austenitic stainless cast steel of the present invention includes C, Si, Mn, Cr, Ni, Nb, N and the like as components thereof.
The contents are as follows:

C: 0.01 - 0.10 percent by mass, preferably 0.02 - 0.04 percent by mass;
Si: 0.6 - 1.0 percent by mass, preferably 0.7 - 0.9 percent by mass;
Mn: 2.0 - 2.8 percent by mass, preferably 2.2 - 2.4 percent by mass;
N: 0.1 - 0.4 percent by mass, preferably 0.15 - 0.25 percent by mass;
Cr: 18.0 - 24.0 percent by mass, preferably 19.5 - 21.5 percent by mass;
Ni: 8.0 - 15.0 percent by mass, preferably 10.5 - 12.5 percent by mass; and
Nb: 0.2 - 0.7 percent by mass, preferably 0.2 - 0.4 percent by mass.

The compositions (percent by mass) of the austenitic stainless cast steel of the present invention, and of CF8C and CF8C-Plus for comparison, are shown in Table 1.

[Table 1]

	Austenitic stainless cast steel of the present invention	CF8C	CF8C-Plus
Ferrite (volume fraction (%))	0.1 - 5.0	12.0	-
C (percent by mass)	0.01 - 0.10	Up to 0.08	0.05 - 0.15
Si (percent by mass)	0.6 - 1.0	Up to 2.0	0.2 - 1.0
Mn (percent by mass)	2.0 - 2.8	Up to 1.5	0.5 - 10.0
Cr (percent by mass)	18.0 - 24.0	18.0 - 21.0	18.0 - 25.0
Ni (percent by mass)	8.0 - 15.0	9.0 - 12.0	10.0 - 15.0
Nb (percent by mass)	0.2 - 0.7	Up to 1.0	0.1 - 1.5
N (percent by mass)	0.1 - 0.4	-	0.05 - 0.5

In the austenitic stainless cast steel of the present invention, by setting the volume fraction of the ferrite phase to 0.1 - 5.0 %, even when the cast steel is exposed to high temperature for a long period of time, the precipitation amount of the sigma phase can be suppressed low. Therefore, the austenitic stainless cast steel of the present invention is unlikely to be embrittled, and exhibits excellent aging ductility.
In addition, the austenitic stainless cast steel of the present invention has a higher Mn content and a lower C content than those of CF8C. With this configuration, the strength and oxidation resistance at high temperature can be improved.
The austenitic stainless cast steel of the present invention can be produced by melting the above-described metal components in a melting furnace and performing cooling from a temperature range of 1,150 - 1,350 °C to a temperature range of 600 - 800 °C at a cooling rate of 30 °C/min or more. By producing the austenitic stainless cast steel of the present invention under the above-described conditions, even when the cast steel is left as-cast, excellent strength property can be obtained, and thus solution heat treatment can be omitted.
The produced austenitic stainless cast steel is used, for example, for piping, valves and the like in chemical plants and power plants.

Example 1

Example of the present invention will be described.

The main components (percent by mass) of the austenitic stainless cast steel of the present invention (Examples 1-1 - 1-6) and CF8C (Comparative Examples 1-1 - 1-5) are shown in Tables 2 and 3, respectively.

[Table 2]

	Example
	1-1	1-2	1-3	1-4	1-5	1-6
Ferrite (volume fraction (%))	0.2	0.2	0.2	0.2	0.2	0.2
C (percent by mass)	0.04	0.03	0.04	0.03	0.08	0.06
Si (percent by mass)	0.76	0.86	0.76	0.86	0.89	0.86
Mn (percent by mass)	2.07	2.15	2.07	2.15	2.07	2.12
Cr (percent by mass)	20.55	19.90	20.55	19.90	22.35	22.10
Ni (percent by mass)	11.38	11.12	11.38	11.12	10.50	10.34
Nb (percent by mass)	0.27	0.26	0.27	0.26	0.29	0.32
N (percent by mass)	0.21	0.20	0.21	0.20	0.19	0.21

[Table 3]

	Comparative Example
	1-1	1-2	1-3	1-4	1-5
Ferrite (volume fraction (%))	12.0	9.0	0	0	0
C (percent by mass)	0.03	0.03	0.017	0.08	0.06
Si (percent by mass)	0.47	0.63	0.37	0.48	0.57
Mn (percent by mass)	1.04	4.48	1.83	1.02	2.02
Cr (percent by mass)	19.98	19.93	19.93	19.35	19.60
Ni (percent by mass)	9.92	9.45	11.63	11.49	11.55
Nb (percent by mass)	0.59	0.42	0.43	0.69	0.71
N (percent by mass)	0.03	0.10	0.24	0.25	0.24

In these Examples and Comparative Examples, aging ductility (700°C - 620 hours), tensile strength (900°C), 0.2% proof stress (900°C) and oxidation resistance (1,000°C) were examined, and further a high-temperature low-cycle fatigue test (alternate triangular waves, strain rate of 0.1%/sec, 700°C, total strain of 0.5%) was performed.

It should be noted that both in Examples and Comparative Examples, casting was performed using normal static casting method. In Examples 1 and 2, the cast steel was left as-cast, while in the other Examples and Comparative Examples, the cast steel was subjected to SHT (solution heat treatment). Aging ductility, tensile strength, 0.2% proof stress, and oxidation resistance were examined and the results are shown in Table 4.

[Table 4]

	Aging ductility (%)	Tensile strength (Mpa)	0.2% proof stress (Mpa)	Oxidation resistance (mm/year)	High-temperature low-cycle fatigue test (times)
Example 1-1	24.4	120	90	0.300	-
Example 1-2	28.8	125	87	0.370	6200
Example 1-3	24.0	113	91	0.066	3400
Example 1-4	29.2	134	89	0.122	2420
Example 1-5	20.4	131	91	0.489	-
Example 1-6	22.1	129	88	0.394	-
Comparative Example 1-1	17.2	93	70	1.278	2388
Comparative Example 1-2	6.8	101	75	3.494	-
Comparative Example 1-3	8.6	127	84	1.854	-
Comparative Example 1-4	11.2	98	73	4.101	-
Comparative	8.2	104	77	3.124	-
Example 1-5

As a result, regarding aging ductility, Examples exhibited 20.4% or more, while Comparative Examples exhibited 17.2% or less.
Regarding tensile strength, Examples exhibited 113 - 134 Mpa, while Comparative Examples exhibited 93 - 127 Mpa.
Regarding 0.2% proof stress, Examples exhibited 87 - 91 Mpa, while Comparative Examples exhibited 70 - 84 Mpa.
Regarding oxidation resistance, Examples exhibited 0.489 mm/year or less, while Comparative Examples exhibited 1.278 mm/year or more.
To sum up, though Examples and Comparative Examples were not notably distinguishable in the 0.2% proof stress, it was found that Example exhibited excellent result in aging ductility, tensile strength and oxidation resistance. Especially, an average value of the aging ductility in Examples was 24.8%, while an average value in Comparative Examples was 10.4%, and thus the value in Example was approximately 2.4 times as high as that in Comparative Example. Likewise, an average value of oxidation resistance in Examples was 0.290mm/year, while an average value in Comparative Examples was 2.770 mm/year, and thus the value in Example was improved approximately 9.5 times as much as that in Comparative Example.
The above-described results shows the case where the volume fraction of the ferrite phase of the austenitic stainless cast steel of the present invention was 0.2%, and it is considered that similar results will be obtained when a lower limit of the volume fraction of the ferrite phase is set to 0.1%.

Example 2

In Example 1, the volume fraction of the ferrite phase of the austenitic stainless cast steel of the present invention was 0.2% (Examples 1-1 - 1-6). In addition, also for a case in which the volume fraction of the ferrite phase is 1 - 3%, aging ductility, tensile strength, 0.2% proof stress and oxidation resistance were examined (Examples 2-1 - 2-4) under the same condition for Example 1. The components of Examples 2-1 - 2-4 are shown in Table 5, and the results are shown in Table 6.

[Table 5]

	Example
	2-1	2-2	2-3	2-4
Ferrite (volume fraction (%))	2	1	3	1
C (percent by mass)	0.014	0.013	0.020	0.013
Si (percent by mass)	0.67	0.72	0.62	0.72
Mn (percent by mass)	2.26	2.37	2.00	2.22
Cr (percent by mass)	21.10	21.10	21.70	22.22
Ni (percent by mass)	11.29	11.38	12.09	11.54
Nb (percent by mass)	0.29	0.29	0.27	0.27
N (percent by mass)	0.22	0.23	0.16	0.23

[Table 6]

	Aging ductility (%)	Tensile strength (Mpa)	0.2% proof stress (Mpa)	Oxidation resistance (mm/year)
Example 2-1	27.0	128	89	0.006
Example 2-2	24.0	123	88	0.058
Example 2-3	27.0	95	63	0.558
Example 2-4	20.4	137	88	0.015

As a result, an average value of aging ductility in Examples 2-1 - 2-4 was 24.6%, and an average value of oxidation resistance was 0.159 mm/year. Like in Example 1, these values are recognized as being excellent over the values in Comparative Example. It is considered that similar results will be obtained when an upper limit of the volume fraction of the ferrite phase of the austenitic stainless cast steel of the present invention is set to 5%.

Example 3

With respect to the austenitic stainless cast steel whose Mn content was approximately 1.0 - 4.5 percent by mass, oxidation resistance (mm/year) was examined. As the austenitic stainless cast steel of the present invention, those with the Mn content of 2.26 percent by mass (Example 3-1) and 2.33 percent by mass (Example 3-2) were used. As the austenitic stainless cast steel of Comparative Example, those with the Mn content of 1.04 percent by mass (Comparative Example 3-1), 1.17 percent by mass (Comparative Example 3-2), 1.81 percent by mass (Comparative Example 3-3), 4.37 percent by mass (Comparative Example 3-4), and 4.48 percent by mass (Comparative Example 3-5) were used. The components for these Examples and Comparative Examples are shown in Table 7. The results are shown in Table 8 and Fig. 1.

[Table 7]

	Example		Comparative Example
	3-1	3-2	3-1	3-2	3-3	3-4	3-5
Ferrite (volume fraction (%))	2	3	12	8	0.2	10	9
C (percent by mass)	0.03	0.03	0.03	0.03	0.017	0.03	0.03
Si (percent by mass)	0.65	0.64	0.47	0.61	0.36	0.62	0.63
Mn (percent by mass)	2.26	2.33	1.04	1.17	1.81	4.37	4.48
Cr (percent by mass)	20.45	20.47	19.98	20.09	19.87	19.87	19.93
Ni (percent by mass)	11.35	11.33	9.92	9.92	12.49	9.35	9.45
Nb (percent by mass)	0.65	0.62	0.59	0.62	0.29	0.66	0.42
N (percent by mass)	0.14	0.12	0.03	0.12	0.20	0.10	0.10

[Table 8]

	Oxidation resistance (mm/year)
Example 3-1	0.5062
Example 3-2	0.4521
Comparative Example 3-1	1.2782
Comparative Example 3-2	2.6405
Comparative Example 3-3	1.7060
Comparative Example 3-4	3.6345
Comparative Example 3-5	3.4943

As can be seen in Fig. 1, in the austenitic stainless cast steel of the present invention where the Mn content is 2.0 - 2.8 percent by mass, oxidation resistance can be reduced to 1 mm/year or less.

Industrial applicability

The present invention is applicable to the production of the austenitic stainless cast steel.

Claims

An austenitic stainless cast steel, wherein
a volume fraction of a ferrite phase is 0.1 - 5.0 %, and

the cast steel consists of: 0.01 - 0.10 percent by mass of C; 0.6 - 1.0 percent by mass of Si; 2.0 - 2.8 percent by mass of Mn; 0.1 - 0.4 percent by mass of N; 18.0 - 24.0 percent by mass of Cr; 8.0 - 15.0 percent by mass of Ni; 0.2 - 0.7 percent by mass of Nb; and the balance is Fe and inevitable impurities.
The austenitic stainless cast steel according to claim 1, wherein the volume fraction of the ferrite phase is 0.5 - 3.0 %.
The austenitic stainless cast steel according to claim 1 or 2, wherein Mn is 2.07 - 2.8 percent by mass and Nb is 0.26 - 0.7 percent by mass.
A method of producing the austenitic stainless cast steel according to any one of claims 1 to 3, the method comprising:
a melting of metal components in a melting furnace, and

a cooling of the molten metal components from a temperature range of 1,150 - 1,350 °C to a temperature range of 600 - 800 °C at a cooling rate of 30 °C/min or more.
A valve formed of the austenitic stainless cast steel according to any one of claims 1 to 3.