© J. Berka and J. Kalivodová, published by EDP Sciences, 2016

1 Introduction

Czech research organizations, universities and industrial companies are involved in High Temperature Reactor (HTR) and also Gas Fast Reactor (GFR) Research program. The examples of these organizations are listed in Table 1. The research used to be supported by the Ministry of Industry and Trade of Czech Republic, presently it is supported by the Technology Agency of Czech Republic. Some of Czech organizations also participate in the international projects aimed to HTR and GFR – as examples the ARCHER [1] and ALLIANCE projects could be named. One of the most important tasks of HTR program is testing and the evaluation of properties and degradation of materials for HTR and other high temperature applications. For these activities, several experimental facilities are used – one of the most significant facility is the High Temperature Helium Loop (HTHL) – the scheme of the device is shown in Figure 1. The main operational parameters of the device are: gas pressure 3–7 MPa, temperature in the test section 25–900 °C, gas flow 12–38 kg.h^–1 (for limited time the gas flow could be even lower than the mentioned lower limit). The gas in the loop should consist of helium with only minor impurities (H₂, H₂O, CO, CO₂, N₂, O₂, CH₄) in concentrations up to approximately 500 vppm. See reference [2] for more details about the device. Another large research infrastructure (and also two new helium loops) is planned to be built in Czech Republic within the SUSEN project [3]. The program of testing the compatibility of metallic alloys with high temperature HTR helium coolant refers to previous activities performed within HTR program in the world (mostly in the last century). Some results are summarized e.g. in references [4–6]. In reference [4], the results from material research within the HTR program in approximately 1960–1990 are summarized, the list of metallic alloys for possible use for HTR components is introduced in this reference. In references [5,6], the high temperature corrosion mechanism of nickel alloys in HTR helium environment is described, the results of corrosion tests of alloys Inconel 617 and Haynes 230 in impure helium at up to 950 °C are summarized.

Fig. 1 Scheme of the High Temperature Helium Loop.

2 Experimental

The high temperature testing program is focused on corundum and cordierite ceramics and special metallic alloys. The first experiments concerning ceramic materials were aimed at electrical properties at high temperature. Ceramics are usually used as an insulating material for heating elements in experimental devices produced in Research Centre Řež and ÚJV Řež. Previously, cordierite ceramics were used for this purpose, but during the test operation of HTHL temperature above ca. 670 °C, it was not possible to reach the higher temperatures with the heating elements insulated by cordierite ceramics, due to rapid decrease of electrical resistance. When the temperature reached 670 °C, the limit of leakage current given by the standard ČSN 33 1610 – see reference [7] for details – was exceeded. The standard ČSN 33 1610 gives the upper limit of leakage current 1 mA per 1 kW of output for devices with output higher than 3.5 kW. Therefore, the new ceramic insulator for heating elements was developed and its electrical resistance depending on temperature in helium environment tested. See references [8,9] for details about the testing of electrical resistance. For the basic properties of tested ceramic materials, see Table 2.

Within the test program also, testing of other types of ceramic materials has begun, e.g. investigation of mechanical properties of ceramics Lunit 73 (C610), Luxal 203 (C799), AG 202 (C795) after log-term exposure in high temperature helium environment (up to 900 °C) is planned. See reference [10] for details about the materials and their manufacturing.

Also the high temperature metallic alloys were tested during the Czech HTR program: Alloy 800 H (WIG welded by Nicrofer S7020), ferritic steel P91 and austenitic steel 316 L. The chemical composition of tested alloys is listed in Tables 3–5.

The specimens were exposed:

• in the quartz retort in the furnace at 750–760 °C (the test temperature was determined – among others – with regard of the submission of the projects within which the tests were performed) for up to 1500 hours at atmospheric pressure in the impure helium environment. The chemical composition of inlet helium gas is listed in Table 6 (composition of premixed gas mixture in pressure vessel, concentration of oxygen in the pressure vessel guaranteed by the producer). Concentration of residual moisture was measured by optical hygrometer in the inlet to the retort and ranged from 1–10 vppm;

  Table 6

  Chemical composition of premixed gaseous mixture used for experiment.

• in High Temperature Helium Loop (HTHL) during the first period of the test operation of the device. The first period of the test operation lasted 264 hours, HTHL was filled with the pure technical helium (purity 4.6; producer determines that concentration of impurities in this helium contains less than 30 vppm of impurities, and less than 5 vppm of O₂). The temperature ranged from 25 to 750 °C, the average temperature was 500 °C. Residual moisture content measured by optical hygrometer in helium gas reached max. 250 vppm, several check sample analyzed by gas chromatography confirmed the concentration of impurities other than O₂ and H₂O was less than 2 vppm. During this period of the test operation of HTHL separate oximeter was not integrated to the gas circuit. See reference [2] for details about the system of helium purity control of HTHL. The gas pressure and gas flow ranged from 2 to 7 MPa and approximately 2–9 g.s^–1 (7.2–32.4 kg.h^–1) respectively. The main parameters during this period of the test operation are illustrated in the graph in Figure 2.

  Fig. 2 Parameters during the first period of the test operation of High Temperature Helium Loop.

After exposure, the degradation of specimens was investigated. Gravimetry, Scanning Electron Microscope (SEM) and theoptical microscope were used for this purpose. The cross-sections of specimens were prepared. The microstructure was further checked by etching by 10% oxalic acid solution. The change of hardness and micro hardness and fracture toughness (only for P91 and 316 L) was also investigated. More details about experiment could be found e.g. in reference [11].

Tests of other alloys, e.g. Inconel 713, 738 and austenitic steel N155, at 900 °C in impure helium environment are also planned. The corrosion test of Alloy 800 H, steel P91 and 316 L in HTHL is in progress.

3 Selected results

3.1 Selected results of tests of ceramics

The electrical resistivity of corundum ceramics at high temperature (up to 900 °C) was proven to be significantly higher than that of cordierite ceramics. The results of the tests are summarized in the graph in Figure 3. The limit of leakage current given by the standard ČSN 33 1610 will not be exceeded even at 900 °C if corundum ceramics is used for insulating the heating elements. Therefore, corundum ceramics C799 is convenient for this purpose.

Fig. 3 Dependence of specific electric resistance of tested ceramic materials on temperature.

3.2 Selected results of tests of metallic alloys

The mass changes of the specimens of alloys exposed in the furnace are summarized in the graph in Figure 4. The uncertainty of the results could be estimated to be about 10%. The mass gain of alloy 800 H was the highest of that of tested alloys.

The oxidation layer on the surface of exposed specimens was mainly formed by chromium and manganese oxides. The spalling of the oxide layer was observed mainly on the surface of the Heat Affected Zone (HAZ) – obviously visible on Figure 5. Thickness of the oxide layer on all tested metallic specimens was in the range 2–4 microns.

The images of microstructure of steels P91 and 316 L before and after exposure are shown in Figure 6 and Figure 7 respectively. Precipitation of particles (carbides) after exposure is apparent (see Figs. 6b and 7b). In case of P91, the subsurface layer without carbides (up to ca. 17 μm thick) appeared after exposure. The microstructure of base metal and weld join of Alloy 800 H before and after exposure is given in Figures 8 and 9. The precipitation of particles after exposure is visible by comparison of these figures. After exposure of 1000 hours, significant precipitation of particles (M₂₃C₆ and γ́) was noticed. Under the corrosive layer ∼20 μm undersurface layer without precipitates was observed. There are some differences in composition of the surface corrosive layer after exposure in the furnace and in HTHL during the test operation – except chromium although a significant percentage of iron and nickel was detected by SEM analysis in the surface corrosive layer on Alloy 800 H after exposure in HTHL. Mass gain of specimen after exposure in HTHL was 0.06 mg.cm^–2. The dependence of hardness and micro hardness of tested materials on exposure time is illustrated in Figure 10.

The fracture toughness of austenitic steel 316 L decreased after exposure of 1000 hours at 750 °C in impure helium of 67% (from value of J_0.2 integral 62 J.cm^–2 in as-received state to 20 J.cm^–2 after exposure). The fracture toughness of ferritic steel P91 almost did not change after exposure. The change of fracture toughness of 316 L is probably caused by changes of material at high temperature independently of environment (e.g. due to the precipitation of the sigma phase after annealing at 750 °C during 1000 h) – however, to prove this assumption, other tests in different environments (e.g. in air) at the same temperature are needed.

Fig. 4 Mass change of the specimens of alloys exposed in impure helium environment at 750–760 °C. BM: base metal, WM: weld metal, HAZ: heat affected zone.

Fig. 5 Spalling of surface layer on welded specimen of Alloy 800 H after exposure of 1500 hours at 760 °C in impure helium.

Fig. 6 Microstructure of steel P91 (the cross-section of the specimen): (a) in as-received state, (b) after exposure in impure helium 750 °C/1000 h.

Fig. 7 Microstructure of steel 316 L (the cross-section of the specimen): (a) in as-received state, (b) after exposure in He 750 °C/1000 h.

Fig. 8 Microstructure of base metal of Alloy 800 H on the cross-section of specimens: (a) in as-received state, (b) after exposure of 1500 hours in impure helium at 760 °C in the furnace, (c) after exposure in HTHL during 264 hours of the test operation.

Fig. 9 Microstructure of interface of weld metal and heat affected zone of alloy 800 H: (a) in as-received state, (b) after exposure of 1500 hours in impure helium at 760 °C.

Fig. 10 (a) hardness, (b) micro hardness of tested alloys depending on exposure time in impure helium at 750–760 °C.

4 Conclusions

The research organizations and industrial companies in Czech Republic participate in the research and development of materials and technologies for High Temperature gas cooled Reactors and other high temperature industrial applications. These activities are supported – among others – by the European Commission within the international FP7 projects and also by the Technology Agency of Czech Republic. The infrastructure for this investigation exists in Czech Republic and is being extended. Some results of investigation of high temperature degradation of metallic and non-metallic materials are already available, other tests and evaluation are still in progress and others are planned.

With regard to metallic materials which were tested so far: stainless steel 316 L proved the best corrosion resistance in impure helium at 750–760 °C, however mechanical properties of this steel changed after exposure at high temperature. Fracture toughness of steel P91 almost did not change after exposure at high temperature. These materials are not designed for long-term operations at such high temperatures; however these materials could be used e.g. for not mechanically loaded parts of experimental devices (for example sample holders) or colder parts. Mechanical properties of Alloy 800 H after exposure at high temperature were not tested. According to obtained results, corrosion resistance of Alloy 800 H at high temperature in impure helium seems to be worse compared to other tested materials.

With regards to tested ceramic materials, corundum base ceramics seems to be a better material as an insulator of heating elements for high temperatures than commonly used cordierite ceramics.

Acknowledgments

The presented work was financially supported by the TACR (Alfa Project TA03010849 and TA03020850) and by the SUSEN Project CZ.1.05/2.1.00/03.0108 realized in the framework of the European Regional Development Fund (ERDF).

The presented work was also supported within the FP7-ARCHER project supported by the European Commission.

The authors also thank colleagues from ÚJV Řež and Institute of Plasma Physics of the Academy of Sciences of the Czech Republic for performing and evaluating some tests on exposed specimens.

References

All Tables

All Figures

	Fig. 1 Scheme of the High Temperature Helium Loop.
In the text

	Fig. 2 Parameters during the first period of the test operation of High Temperature Helium Loop.
In the text

	Fig. 3 Dependence of specific electric resistance of tested ceramic materials on temperature.
In the text

	Fig. 4 Mass change of the specimens of alloys exposed in impure helium environment at 750–760 °C. BM: base metal, WM: weld metal, HAZ: heat affected zone.
In the text

	Fig. 5 Spalling of surface layer on welded specimen of Alloy 800 H after exposure of 1500 hours at 760 °C in impure helium.
In the text

	Fig. 6 Microstructure of steel P91 (the cross-section of the specimen): (a) in as-received state, (b) after exposure in impure helium 750 °C/1000 h.
In the text

	Fig. 7 Microstructure of steel 316 L (the cross-section of the specimen): (a) in as-received state, (b) after exposure in He 750 °C/1000 h.
In the text

	Fig. 8 Microstructure of base metal of Alloy 800 H on the cross-section of specimens: (a) in as-received state, (b) after exposure of 1500 hours in impure helium at 760 °C in the furnace, (c) after exposure in HTHL during 264 hours of the test operation.
In the text

	Fig. 9 Microstructure of interface of weld metal and heat affected zone of alloy 800 H: (a) in as-received state, (b) after exposure of 1500 hours in impure helium at 760 °C.
In the text

	Fig. 10 (a) hardness, (b) micro hardness of tested alloys depending on exposure time in impure helium at 750–760 °C.
In the text