Austenitic steel having superior characteristics in resistance against stress corrosion cracking, method for producing of same and usage of same

Abstract: The present invention relates to an austenitic steel comprising Ni of 9 - 30 %, Cr of 10 - 23 %, and Fe of at least 45 %, which is characterized in comprising enough Cr and Ni to form whole austenitic structure in the equilibrium diagram at 700 °C, having austenitic phase at room temperature, and said austenitic phase is a single crystal, and has superior resistance against stress corrosion cracking. The austenitic steel is preferably comprising C ≦ 0.1 %, Si ≦ 1 %, Mn ≦ 2 %, Ni 9 - 15 %, Cr 16 - 18.5 %, and at least one of elements selected from the group of Mo 1 - 3 %, Ti 0.05 - 1 %, and Nb 0.1 - 1.5 %, as of an alloy composition. The alloy relating to the present invention is preferable as a material for members of a reactor core of a nuclear reactor.

Description: The present invention relates to a new stainless steel of austenitic group, method for producing of same and usage of same, and especially relates to the stainless steel of austenitic group for a structural material which is preferably used under an environment of radiation irradiation in a reactor core of a nuclear reactor and of a nuclear fusion reactor, and also relates to method for producing of same and usage of same. A stainless steel of austenitic group, especially the stainless steel of high chromium-nickel type is widely used as a material in manufacturing of structural members which are used in the nuclear reactor because that the stainless steel has preferable resistance to corrosive environment in addition to have a preferable characteristics as the structural material. But, the member made of stainless steel of austenitic group which is used in the reactor core of a light water reactor etc. increases its sensitivity to intergranular stress corrosion cracking (IGSCC) with long time irradiation in use in the reactor. For example, while the stainless steel having solid solution state obtained by solution treatment has resistivity to intergranular stress corrosion cracking at outside of the reactor core, the same material loses the resistivity when the material is irradiated in the reactor core to high level dose, especially to at least 0.5 x 10 21 n/cm 2 in neutron irradiation dose. As the cracking described above is induced by irradiation, it is called irradiation assisted stress corrosion cracking (IASCC) and is currently becoming a problem at old nuclear reactors. As one of the methods to solve the problem, a prior art to adjust contents of constitutive elements of stainless steel of austenitic group, such as N, P, Si, S, C Mn, Cr, and Ni, and to add small amount of Ti and Nb as well to the stainless steel is disclosed in JP-A-63-303038 (1988). Further, a two phase stainless steel having dispersed γ phase in single crystal of α phase and superior characteristics in resistance against stress corrosion cracking is disclosed in JP-A-62-180038 (1987). Nevertheless, as the invention disclosed in JP-A-63-303038 (1988) uses a polycrystalline stainless steel as same as a conventional method in manufacturing of the members, and the members have a plurality of grain boundaries which will become sources of the irradiation assisted stress corrosion cracking. Therefore, although the resistance against stress corrosion cracking itself is increased, it is impossible to prohibit substantially the cracking which is induced by irradiation. Further, the invention disclosed in JP-A-62-180038 (1987) uses single crystal for α phase and improves resistance against the stress corrosion cracking which is caused by irradiation induced embrittlement, but as the σ phase is easily formed at high temperature, enough stability can not be obtained and the resistance against the corrosion itself is not sufficient. Moreover, the material has problems of high ductile-brittle transition temperature and low toughness, which is especially indicated as low impact value. Stress corrosion cracking of a single crystalline material of type 304 steel in H 2 SO 4 -NaCl solution was disclosed in page 770 -774 of the Journal of the Metallic Society of Japan, volume 43 (1979). Nevertheless, as the type 304 steel is sensitive to irradiation induced embrittlement by neutron irradiation in the nuclear reactor, decreasing of elongation rate and increasing of hardness are caused and, therefore, low resistance against irradiation assisted stress corrosion cracking becomes a problem. Further, martensitic phase is easily formed by working such as cutting because of instability of austenitic phase in the type 304 steel, and consequent lowering of corrosion resistance is a problem. And, manufacturing of single crystalline members of type 304 steel having large diameter of about 10 mm is very difficult, and manufacturing of larger members than diameter of 10 mm is almost impossible. Moreover, the steel has a problem to cause stress corrosion cracking by heating at a range of temperature to precipitate carbide as the steel has high carbon content of about 0.08%. Chem. Abstr. vol. 108, No. 11, 14 March 1988, abstract 99480q and JP-A-62-180037 disclose an austenitic group alloy having superior stress corrosion cracking characteristics, which has a composition, in % by weight; Cr 18-35 Ni 25-50 Mo 0-8% Mn 0.6% N at most 0.5% C at most 0.03% Si at most 0.2% P at most 0.015% S at most 0.005% Balance Fe Journ. Metallic Soc of Japan, vol. 43, 1979, page 770-774 discusses the characteristics of stress corrosion cracking of type 304 steel single crystals in H 2 SO 4 -NaCl solution. EP-A-0288245 discloses an austenitic stainless steel alloy in which the following are observed; N up to 0.05% C 0.025 to 0.067% Mn 1.5 to 2.0% P up to 0.005% Si up to 0.05% S up to 0.005% and preferably Cr 15-30% Ni 5-15% In EP-A-0288245 it is stated that a reduction in the susceptibility to IASCC is essentially achieved by controlling the nitrogen content to a maximum of 0.05%, preferably 0.03% The aim of the present invention is to provide stainless steel of austenitic group which has an enough phase stability, easiness in manufacturing, and superior characteristics in toughness and resistance against irradiation assisted stress corrosion cracking, and the method for producing of same, and also to provide nuclear reactor members which have a long life in an environment under radiation level like in the reactor core, and the reactor core of same. The present invention therefore provides to an austenitic steel as set out in claim 1. The austenitic steel relating to the present invention can include ferritic phase. The ferritic phase may be 0.1-20% in area fraction, preferably 0.1-10%. The present invention also relates to articles made of a steel as set out in claim 1. Such articles include members of nuclear reactor cores such as upper grid plates, core supports and bolts. When using a material of a single crystal contacted and combined with polycrystalline material, corrosion can be prevented by selecting the same kind material because of eliminating the difference of potentials between the two materials in the reactor environment. A single crystalline material is made from an original polycrystalline material which is used in the present reactor. Especially, difference in composition of the single crystalline material and the polycrystalline material is preferably at most 5 % in Ni content and at most 3 % in Cr content. Further, the difference is preferably at most 0.05 % in C content, at most 0.5 % in Si content, at most 1 % in Mn content, and at most 1 % in Mo content. The present invention also provides a method for producing austenitic steel as set out in claim 5. That is, the present invention is achieved by manufacturing of structural members with the stainless steel having austenitic phase of a single crystal which is produced by the steps of melting of chromium-nickel type austenitic group stainless steel having a specific composition, solidifying from one side, and further homogenizing by heat treatment on the members after cutting work or without the cutting work to make the austenitic phase a single crystal. In the case described above, the stainless steel is melted at temperature of 1500 - 1650 °C in reduced pressure of lower than 3 x 10 -3 Torr or in inert gas atmosphere, and the solidification from one side is performed by the steps of setting a mold at inside of a mold heating furnace which is placed on a water cooled chiller, heating the mold at 1500 - 1650 °C, casting the molten stainless steel into the mold, leaving a several minutes, withdrawing the mold gradually from the mold heating furnace. The withdrawing is performed in reduced pressure of lower than 2 x 10 -3 Torr or in inert gas atmosphere, and by the solidifying rate of 1 - 50 cm/h. Subsequent solution heat treatment, namely homogenizing heat treatment, is performed at least once at 1000 - 1350 °C, for example, by a method to keep 5 hours at 1350 °C and following one hour at 1100 °C in argon gas atmosphere, and subsequently to quench in cold water. Stress corrosion cracking of austenitic stainless steel which is to be overcome by the present invention is generated almost all at grain boundary. Therefore, reduction of the stress corrosion cracking can be achieved with a method to prevent generation of the stress corrosion cracking by making members of stainless steel have no grain boundary or, if ferritic phase is existing, make the ferritic phase dispersed into a single crystal of the austenitic phase. Accordingly, inventors of the present invention investigated methods to produce austenitic stainless steel having no grain boundary, and performed a test of stress corrosion cracking in an environment of high temperature and high pressure water simulating interior of the nuclear reactor, and found a following method to obtain stainless steel having no grain boundary and more difficulty in generating the stress corrosion cracking in comparison with polycrystalline stainless steel. That is, by melting once of austenitic stainless steel and subsequently solidifying of the molten steel gradually from one side in one direction, crystalline grains having an uniform crystal orientation grow from solidified plane and, after the solidification is completed, stainless steel having not grain boundary, so called a single crystal, can be produced. Melting of austenitic stainless steel is preferably performed at the lowest 1500 °C which is the temperature enable to melt easily, and at the highest 1650 °C which is the temperature enable to retard a reaction with the mold. Further, for avoiding mixing of the molten steel with gaseous elements in air, atmosphere is maintained at reduced pressure of lower than 3 x 10 -3 Torr or in inert gas atmosphere such as argon etc. And the condition to solidify in one direction is such as that the atmosphere is the same as melting by the same reason and the solidifying rate is 1 - 50 cm/h because of producing of a single crystal ingot for a large size members is difficult at a rate of more than 50 cm/h, and the solidifying rate is preferably selected faster than 1 cm/h as the reaction with the mold to cause defects is concerned at a rate of slower than 1 cm/h. The reason to choose the temperature of heat treatment for homogenization at 1000 - 1300 °C is such as that a temperature below 1000 °C is insufficient in eliminating of segregation and heterogeneity of constitutive elements in the crystal and a temperature higher than 1300 °C will cause partial melting of the crystal. The heat treatment for homogenization is preferably performed at least once at a temperature in a range of 1000 - 1300 °C depending on kind of the stainless steel and size of the ingot or the members. Ferritic phase can be eliminated by performing the heat treatment for homogenization at high temperature. As described above, the stress corrosion cracking generated from grain boundary can be prevented or reduced by the method to eliminate grain boundary in the material. The reason to generate intergranular stress corrosion cracking in polycrystalline austenitic stainless steel which is irradiated by high level radiation in water environment of high temperature and high pressure is considered depending on change of structure and composition at the grain boundary, but detail is not clarified yet thoroughly. The present invention is characterized in eliminating grain boundary which cases essentially the problem of generating the cracking. C (carbon) is effective for strengthening of the steel and is contained at most 0.1 %. As the steel is strengthened by making the austenitic phase a single crystal, the content of C is preferably at most 0.03 % in relation with other materials. Especially, a range of 0.010 - 0.025 % is preferable in view of strength and a carbon content which does not cause precipitation of carbide even though the steel is exposed to heat history at carbide yielding temperature. Si and Mn are added as deoxidizers, and further Mn is added as a desulfurizing agent. Si is contained at most 1 % and Mn is contained at most 2 %. Especially, in view of stress corrosion cracking, the content of Si is at most 0.1 % or not added, preferably 0.01 - 0.05 %, and 0.1 - 0.5 % is preferable in a part where the cracking is not severe. And the content of Mn is desired high in aspect of the stress corrosion cracking, but as spoiling of other characteristics is concerned, a range of 0.3 -1.5 % is preferable. Especially 0.2 - 1.0 % is more preferable. Cr is necessary for strengthening of corrosion resistance, forming of austenitic phase, and making the austenitic phase a single crystal for manufacturing of large members, and is contained at least 10 %. But, as large amount of Cr over 23 % forms a large amount of ferritic phase, production of a large single crystalline casting becomes difficult. Especially, 16 - 18.5 % is preferable in relation with amount of Ni. Ni is contained at least 9 % for stabilizing of austenitic phase and strengthening of corrosion resistance. On the contrary, the content over 30 % is not preferable because such large amount of Ni enlarges difference is component composition remarkably from other members of austenitic steel and will be a cause of corrosion of the other members in the same environment. Especially, in production of a large size members from a single crystalline casting of austenitic phase, containment of enough amount of Ni and Cr to form whole austenitic structure in the equilibrium diagram at 700 °C as shown in figure 1 is indispensable in relation with amount of Cr described above. Especially, although preferable Ni content is 9 - 15 % , 12 - 15 % is more preferable. Mo is an effective element to raise corrosion resistance and strength, and may be present in an amount of at least 1%. But addition of more than 3% is not desired. Especially, 2 - 3 % is preferable. Addition of Mo is effective against stress corrosion cracking and embrittlement by neutron irradiation. An alloy containing Mo is most preferable because the alloy is manufactured easily and phase stability of the alloy is maintained. Further, Nb and Ti are also effective elements to raise strength and corrosion resistance, and addition of Nb of 0.1 - 1.5 % and Ti of 0.05 - 1 % is desirable. Among the elements described above, addition of Nb at least 10 x C (%) and Ti at least 5 x C (%) are preferable. Addition of the former of 0.2 - 0.6 % and the latter of 0.05 - 0.3 % is preferable. Austenitic phase has a stable structure to environment and is necessary for obtaining a large size single crystal. The austenitic phase is able to contain ferritic phase of 0.1 - 20 % in area fraction, but whole austenitic phase can be formed. Presence of ferritic phase is desirable for preventing crack generation at solidification in forming a large casting. Especially, presence of 1 - 5 % is preferable. A single crystal of whole austenitic phase can be obtained as it is cast by adjusting composition of the alloy, and, even though ferritic phase is contained in the austenitic phase at solidification, the ferritic phase can be eliminated by performing of solution heat treatment. The single crystal of whole austenitic phase has an advantage to be usable as it is after cutting work because structure of the crystal is stable. The steel related to the present invention can be added at most 5 % of work by bending etc. without changing to polycrystalline. The steel related to the present invention can be used not only in the reactor core of the nuclear reactor but also in a water cooled environment and a hydrogen existing environment, and is applied to structural members which are exposed to radiation, especially is applied to a blanket cooling tube and shell for the first wall of the nuclear fusion reactor. The cooling tube has a water cooling or a He cooling structure, and a pipe composed of protecting material such as W and graphite etc. is inserted on the outer surface side of the tube faced to plasma. By the present invention, generation of irradiation induced intergranular stress corrosion cracking on structural members which are made of austenitic stainless steel and are used under the environment of high irradiation dose of radiation such as the reactor core can be prevented, and extension of using life of members for the nuclear reactor core structure, the first wall and the blanket structure of the nuclear fusion reactor become possible, and consequently distinguished effects to make the nuclear reactor usable for 40 years and to increase safety and reliability of the nuclear fusion reactor. Figure 1 is the equilibrium diagram of a ternary alloy of Fe-Ni-Cr group at 700 °C, Figure 2 is a schematic cross section to show the composition of an apparatus which was used for production of austenitic stainless steel related to the present invention, Figure 3 is a microscopic photograph showing the metallic structure of the austenitic steel related to the present invention, Figure 4 is a schematic perspective illustration to show the testing method to stress corrosion cracking, Figure 5 is a partial cutaway perspective illustration to show the reactor core of an embodiment using austenitic steel related to the present invention, Figure 6 is a partial cutaway plan view of the upper grid plate, Figure 7 is a schematic cross section at VII plane of figure 6, Figure 8 is an enlarged cross section of VIII part of figure 7, Figure 9 is a partially enlarged view of the upper grid plate, Figure 10 is a partially enlarged view of X in figure 9, Figure 11 is a partially enlarged view of XI of figure 9, Figure 12 is a schematic cross section of the reactor core support plate, Figure 13 is a perspective view of the fuel support fitting, Figure 14 is a cross section of the peripheral fuel support fitting, and Figure 15 is an enlarged view of XV in figure 12. Embodiment 1 An embodiment of a method to produce austenitic stainless steel related to the present invention is explained with using figure 2. An apparatus shown in figure 2 is composed of a high frequency induction furnace 2 to produce molten metal 1, a mold heating furnace 8 having a casting inlet 7 which covers a mold 3, a body 4, a selector 5, and a starter 6, and the starter is installed on a water cooled chiller 9. The mold 3 was fixed on the water cooled chiller 9 and was heated to 1550 °C with the mold heating furnace 8. Molten metal 1 was produced by melting of austenitic stainless steel with the high-frequency induction furnace 2 and was casted into the mold 3 through the casting inlet 7. Casting temperature was 1550 °C, and the molten metal in the body 4 was kept at 1550 °C for 5 minutes after the casting, and then the water cooled chiller 9 was descended downward 10 gradually. And finally the mold 3 was withdrawn from the mold heating furnance 8 and the molten metal in the body 4 was solidified in one direction from the water cooled chiller 9 side. The mold heating furnace 8 was kept 1550 °C till the solidification in one direction was completed. The withdrawing rate of the mold was kept constant at 20 cm/h, and the molten metal in the body 4 was kept in atmosphere at reducing pressure of 1 - 3 x 10 -3 Torr. After the casting, a polycrystalline portion where crystals were orientated to one direction was formed by solidifying the molten metal in one direction upward from the water cooled chiller 9 with the starter 6, and concurrently, the size of the polycrystalline portion was adjusted to the size of solidification portion of the selector 5. Solidification was proceeded gradually with withdrawing of the mold 3 downward 10 and during the solidification went on through the selector 5, the crystals concentrated to one crystal and a single crystal was obtained in the part 4 of molten metal in the body. The selector 5 is a mold of a helical shape having straight line sides or zigzag shape. The withdrawing rate of the mold 3 and temperature gradient for solidification near a boundary of the mold heating furnace 8 were controlled, and a single crystal having 20 mm in diameter and 20 cm in length was obtained. The casting was regulated so as to orientate the direction of the solidification to <100> direction. The obtained single crystal was examined by macro-etching. As austenitic stainless steel, SU316 (containing Mo), SUS316L (low carbon, containing Mo), SUS321 (containing Ti), SUS347 (containing Nb) and their improved materials shown in table 1 as No. 1 - 14 were used. As a result, castings having a single crystal of austenitic phase were produced from all kind of steels shown in table 1 as No. 3 - 14. Number of the straight line sides of the helical or zigzag shape of the mold of the selector 5 is selected so as to make one crystalline orientation. Moreover, even though temperature of molten metal altered from 1500 °C to 1650 °C, single crystals of austenitic phase were obtained from the all kind of steels described above. But SUS304 and 304L, both of which had low Ni and high Cr, as designated as No. 1 and No. 2 did not become single crystals. In case of altering the atmosphere at producing of the molten metal 1 and solidifying is one direction of the molten metal to high vacuum under 1 x 10 -3 torr. or inert argon atmosphere, single crystals of good quality which did not include gases such as nitrogen etc. were obtained from the all kind of steels described above. Further, single crystals were also obtained even though the withdrawing rate of the mold at the solidification in one direction were changed in a range of 1 - 50 cm/h. Figure 1 is the equilibrium diagram at 700 °C of Cr-Ni-Fe containing C of about 0.1 %, Si of about 0.5 %, and Mn of about 1 %. SUS 304 and 304L designated as No. 1 and 2 respectively have each of α+γ phase and σ+γ phase at 700 °C, and single crystals are not obtained as the metal causes phase change during the cooling process. But as described above, austenitic steel of No. 3 - 14 related to the present invention are able to be obtained as a single crystal of austentic phase (γ). In the figure 1, point A is Ni 9.0 %, Cr 18.5 %, point B Ni 9.5 %, Cr 15.5 %, point C is Ni 11.5 %, and point D is Ni 23.0 %. Low Ni and low Cr side of a dotted line connecting the point B and the point D is not preferable because of generating martensitic phase during cooling. Figure 3 is a microscopic photograph showing the sample No. 4 in magnification of 100. As showing in the figure, a single crystalline austenitic steel contains ferritic phase of about 3 % in area fraction and single crystal of austenitic phase. Alloys related to the other embodiments also contained ferritic phase in a range of 0.5 % - 10 %. By scaling up of the apparatus showing the figure 2, and as a result of producing a rod of 40 mm in diameter and 1 meter long and a slab of 40 mm thick, 20 cm wide and 1 meter long both of which have a composition as shown as No. 4 in the table 1 by solidification in axial direction as described above, both of the rod and the slab having single crystalline austenitic phase which contains ferritic phase of about 3 % could be produced. That is, by the present invention, a casting having a single crystalline austenitic phase as large as usable for a structural material of at least 20 mm 2 in cross section perpendicular to the axis of solidifying direction can be obtained, and further, a composition which enable to produce larger materials having a cross section more than 2 cm 2 is provided. Therefore, by using of a composition of high nickel side of at least 9 % and of chromium of preferably less than 20 %, a large size casting can be obtained. After the 14 samples produced in the embodiment were treated for homogenization by heating at 1050 °C for one hour and subsequent water cooling, a test piece of 10 mm wide, 50 mm long and 2mm thick was cut out from each of the samples, and CBB test which effective as a testing method for stress corrosion cracking was performed with commercial SUS 316 and 304 steel. Any significant change in structure could not be observed after the heat treatment for homogenization except the ferritic phase decreased a little and shape of the ferritic phase changed to be more round. The ferritic phase could be eliminated by raising the temperature of the heat treatment for homogenization to at least 1200 °C. Figure 4 is a schematic perspective illustration to show the method of CBB testing. A test piece 11 was held with graphite fiber wool 12 to cause gap between holders 13, bolts were inserted through holes 14 for bolts, tightened the test piece with a curve between the holders 13, and performed a test of stress corrosion cracking in an autoclave. Test condition was 288 °C in temperature and immersed for 500 hours in pure water of high temperature and high pressure of 85 kg/cm 2 (including 8 ppm of dissolved oxygen). After the test, the test piece was took out from the autoclave and was examined existence of cracking on surface of the test piece. Although all of the commercial polycrystalline SUS 316 and 304 steel, and test piece of No. 1 and 2 were found to have crackings of 1 - 2 mm in depth, any of crackings were not observed on the 12 single crystalline test pieces of No. 3 to 14 which were produced by the method of the present invention, and superior resistance against stress corrosion cracking was revealed. All of the test pieces were treated for sensitization by heating at 621 °C, 24 hours before the test for stress corrosion cracking. Although precipitation was observed in the ferritic phase after the sensitization treatment, any of precipitation was not observed in the austenitic phase. And a typical result of tensile test on the test piece of No. 4 having a parallel part of 6 mm in diameter is shown in table 2. As shown in the table 2, the strength of the material of single crystal related to the present invention was inferior to the material of polycrystal to some extent, but was still sufficient for use. The polycrystalline material had almost the same chemical composition as the single crystalline material. Tensile strength (kg/mm 2 ) 0.2 % proof stress (kg/mm 2 ) Elongation percentage (%) single crystal 47.9 17.1 50 polycrystal 55.5 20.1 80 Embodiment 2 The casting of single crystalline austenitic stainless steel of No. 4 of the present invention which was produced by the method of the embodiment 1 was treated thermally for homogenization at 1050 °C for one hour, and subsequently, various kind of structural members for the reactor core of the boiling water reactor shown in figure 5 were manufactured from the casting. The nuclear reactor is operated at 288 °C in steam temperature and 70.7 atm in steam pressure, and is possible to generate electric power of 500, 800, and 1100 MW as output. Name of parts are as following: 51...poison curtain, 52...reactor core support plate, 53...neutron detecting instrument, 54...control rod, 55...reactor core shroud, 56...upper grid plate, 57...fuel assembly, 58...upper panel spray nozzle, 59...vent nozzle, 60...pressure vessel lid, 61...flange, 62...instrumentation nozzle, 63...steam separator, 64...shroud heat, 65...feed water entrance nozzle, 66...jet pump, 68...steam dryer, 69...steam outlet nozzle, 70...feed water sparger, 71...reactor core spray nozzle, 72...lower reactor core grid, 73...recycled water entrance nozzle, 74...buffle plate, 75...control rod guide tube. The upper grid plate 56 has a rim body 21, flanges 22 and a grid plate 35, and the members described above are composed of, for example, polycrystalline rolled material which contains Mo and is the same kind material as the material of the single crystal of No. 4 in the table 1. The grid plates 35 are only crossing each other but not fixed. And, the reactor core support plate 52 is composed of, for example, the polycrystalline rolled material containing Mo of No. 4, and is made of a sheet of rolled plate which is provided holes for installing fuel support fittings, and fixed to the reactor vessel at circumferential plane. Therefore, all of the members described above have structures, of which central part are exposed to neutron irradiation, having no welded part. Figure 6 is a partial cutaway plan view of the upper grid plate. Figure 7 is schematic cross section at VII-VII plane of figure 6 and figure 8 is an enlarged cross section of VIII part of figure 7. An alloy related to the present invention was applied to the bolt 23 shown in figure 8. The bolt 23 of the present invention was used for fixing the rim body 21 and upper flange 22, and was manufactured by cutting work of screw thread on a rod shaped material. As formation of polycrystalline phase on surface after the cutting of thread, in which the longitudinal direction of the bolt was 100 , was assumed, solution treatment at 1200 °C for 30 minutes in unoxidizing atmosphere was performed on some of the bolts. Figure 9 is a partially enlarged view of the upper grid, figure 10 is a partially enlarged view of X in figure 9, and figure 11 is a partially enlarged view of XI of figure 10. The bolt and the nut to tightened and fix the grid plate 31 and the support plate 32 of the upper grid plate 56, and the bolt 36 and the nut 37 to tighten the grid plate 31 and the support plate 32, and the support plate 32 and the grid plate 35 were made of single crystals which were produced by the same method as described above in two ways of as it was and as it was treated for solution after the cutting work. Figure 12 is a schematic cross sectional illustration of the reactor core support plate 52 which is furnished with the fuel support fitting shown in figure 13, the peripheral fuel support fitting 44 shown in figure 14, and the eye bolt 42 shown in figure 15 which is an enlarged view of XV in figure 12. And the members shown in figure 13 to 15 were made of single crystalline austenitic steel casting of the present invention as described above as the No. 4 alloy. Further, the pin of the reactor core support plate, which was attached to the reactor core support plate 41, and the washer 43 shown in figure 15 were also made of single crystals using the No. 4 alloy. The members shown in figure 13 and 14 were castings which were solution treated as described above, and the member shown in figure 15 was as it was after the cutting work of thread. The members obtained by the method of the present invention as described above were irradiated to 1 x 10 22 n/cm 2 (> 1 MV) in neutron dose under a condition which simulated an interior condition of the boiling water type nuclear reactor. As a result, stress corrosion cracking which would be induced by irradiation was not observed on any of the bolts and the nuts. The result means that the members can be used 40 years without changing the upper grid plate and the reactor core support plate. Especially, it is important to compose components, which are used under high neutron irradiation dose as 2 x 10 21 n/cm 2 with high stress like the bolt and the nut at a place where surface of the component is impossible to be observed directly, with members having high resistance against stress corrosion cracking which will be induced by irradiation embrittlement. Moreover, it is necessary to use members having the nearly same or similar chemical composition of materials with co-existing structures in aspect of keeping an equal potential each other in water environment with high temperature and high pressure. Even though a single crystal was used for the bolt and the nut in the present embodiment, it is remarkably effective to use the single crystal of the same materials for the grid plate 35 of the upper grid plate and the reactor core support plate 52.

Claims: Austenitic steel having a single crystal austenitic phase, and optionally a ferritic phase, at room temperature, and consisting of, by weight percent, C at most 0.1 % Si at most 1 % Mn at most 2 % Cr 10 to 23 % Ni 9 to 15 % Optionally Mo 1 to 3 % Optionally Nb 0.1 to 1.5 % Optionally Ti 0.05 to 1 % the remainder being Fe and incidental impurities, the amounts of Cr and Ni being sufficient to form a fully austenitic structure in the equilibrium diagram at 700°C. An austenitic steel according to claim 1 having both of an austenitic phase and a ferritic phase. An austenitic steel according to claim 1 comprising Cr of 15 - 18.5 % by weight. An austenitic steel according to claim 1 comprising Cr of 16 - 18.5 % by weight; and having an austenitic phase of at least 80 % and a ferritic phase of 0.1 - 20 % in area fraction. Method for producing an austenitic steel consisting of, by weight percent, C at most 0.1 % Si at most 1 % Mn at most 2 % Cr 10 to 23 % Ni 9 to 15 % Optionally Mo 1 to 3 % Optionally Nb 0.1 to 1.5 % Optionally Ti 0.05 to 1 % the remainder being Fe and incidental impurities, the amounts of Cr and Ni being sufficient to form a fully austenitic structure in the equilibrium diagram at 700°C, comprising the steps of forming molten metal of the austenitic steel which has the fully austenitic structure in the equilibrium diagram at 700 °C; forming a solidified part which is oriented in one direction by solidifying the molten metal of the austenitic steel at initial stage of solidification in one direction; forming a selective solidified part where a single crystal is selectively solidified next to the solidified part; and obtaining a single crystalline casting of austenitic phase by solidifying sequentially in one direction along the oriented direction of the single crystal. A method according to claim 5 for producing an austenitic steel comprising the additional step of performing solution treatment of homogenize the alloy composition of the single crystalline casting. Method according to claim 5 for producing an austenitic steel comprising performing of solution treatment of the single crystalline casting after cutting work. A member of a reactor core of a nuclear reactor which is exposed to water of high temperature and high pressure and also to neutron radiation by burning of nuclear fuel: characterized by being composed of an austenitic steel according to any one of claims 1 to 4. An article which has superior characteristics in resistance against stress corrosion cracking: characterized by being composed of an austenitic steel according to any one of claims 1 to 4. A bolt comprising an austenitic steel according to any one of claims 1 to 4. A reactor core of a nuclear reactor having an upper grid plate and a core support plate: characterized that said upper grid plate and said core support plate are composed of an austenitic steel having substantially identical compositions, each according to any one of claims 1 to 4; all bolts used for assembling of said upper grid plate, eye bolts used for said core support plate, metal fittings for a fuel support, and metal fittings for a peripheral fuel support are composed of an austenitic steel according to any one of claims 1 to 4 having substantially identical composition as said austenitic steel of said upper grid plate. A reactor core of a nuclear reactor having an upper grid plate and a core support plate: characterized that all bolts used for assembling of said upper grid plate, eye bolts used for said core support plate, metal fittings for a fuel support, and metal fittings for a peripheral fuel support are composed of an austenitic steel according to any one of claims 1 to 4.

Inventors: AONO YASUHISA, IKEDA SHINZOO, IZUMIYA MASAKIYO, KATO TAKAHIKO, KODAMA HIDYO, SATO HISASHI, YAMAMOTO MICHIYOSHI, YOSHINARI AKIRA, AONO, YASUHISA, IKEDA, SHINZOO, IZUMIYA, MASAKIYO, KATO, TAKAHIKO, KODAMA, HIDYO, SATO, HISASHI, YAMAMOTO, MICHIYOSHI, YOSHINARI, AKIRA
Applicants: HITACHI LTD, HITACHI, LTD.
Application year: 1991
Main classification: C30B11
IPC codes: C22C30, C22C38, G21C5, C30B11, G21C3