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deposited at the cold zone, and the elements concentration in the liquid metal represents a steady–state balance between the rates of solution and precipitation in different zones of corroding systems [3]. For austenitic stainless steels, it is well documented (for example, Gorynin et al. [2]) that corrosion resistance is determined by oxygen thermodynamic activity in lead and lead alloys. For oxygen concentrations lower than the concentration at which the dissolved oxygen is in equilibrium with the spinel formation on the steel surface materials, dissolution occurs. This equilibrium value is about 5 × 10 -8 wt% at 550ºC. For concentrations higher than this value, materials oxidation appears. Steel composition has also a significant influence in the corrosion/protection of structural materials. In general, it is accepted that in absence of oxygen, carbon steels present a higher corrosion resistance than high chromium steels, which suffer attack [4]. However, results obtained by Gorynin [13] point out that at 460ºC, in flowing Pb-Bi with oxygen concentration less than 10 -7 wt%, 1Cr-MoV alloy presents higher corrosion rate than 18Cr-10Ni-Ti alloy, whereas 1Cr-2Si-Mo is more resistant to corrosion than both the previous ones. For high oxygen activity the corrosion of iron–chromium alloys is higher than for iron whereas for low oxygen activity the alloy presents higher resistance corrosion. Formation of oxide layer on the structural materials can prevent alloy dissolution. A general consideration of the results seems to point out that the oxygen content in the loop is not enough to form, in general, protective oxide layers on the specimens placed in the hot zone of the loop. In fact, specimens B, C (F82H) and Q, R (2¼ Cr-Mo) present material dissolution and no oxide layers. However, in the type A (F82H) and P (2¼ Cr-Mo) specimens tested from the beginning of the operation, an appreciable growth of the oxide layer was detected. It seems that A and P samples are in oxidation condition whereas the rest of the specimens would be in dissolution conditions. This observation would mean that, although the gas is bubbling during all the operation time with the same flow rate and the same oxygen content (10 ppm), the oxygen concentration in the liquid lead-bismuth varies along the operation time and so does the corrosion behaviour of the samples. Type A specimens (F82H) inserted into the loop at the beginning of the operation are covered by an homogeneous double oxide layer. The thickness of this oxide layer reaches 20 µm after 3 022 hours. The growth of this oxide layer is almost inappreciable between 340 and 1 030 hours, and then it grows significantly up to 3 022 hours. These results seem to be in accordance with the general behaviour accepted for the oxidation of iron-chromium alloys and stainless steels [5]. After an initial protective period, a sudden rate increase occurs once the break-away time has been reached. This stage is often followed by a further rate reduction by a self-healing process. This last step has not been observed in our tests, probably due to their short duration. The oxide layers of type A specimens show similar characteristics. The inner oxide layer, Fe (Fe 2-x )Cr x O 4 , seems to be protective enough to prevent lead-bismuth penetration. No eutectic is incorporated to this layer contrary to the observed in iron oxide outer layer. Eutectic concentration in the outer layer decreases and disappears in the interface outer/inner oxide layer. Type P specimens (2¼ Cr-Mo) inserted into the loop at the beginning of the operation are covered by a non-adherent oxide layer with a wrinkled aspect. Labun et al. [6] describe a layer with these characteristics for a 3Cr-Fe steel oxidised in dry oxygen at 700-800 ºC. They say that the wrinkling is due to a substantial growth of this layer in the lateral direction relative to the underlying layers. In our case, lead-bismuth penetrates through the external oxide layer and is place between it and the steel. The layer formed on 2¼ Cr-Mo specimens is much thicker in all the cases that the formed on type A specimens. Fedirko et al. [7] tested Armco iron, Fe-16Cr and Fe-16Cr-1Al in stagnant liquid lead at 600ºC with some amount of lead oxide to get a concentration of 10 -5 wt% oxygen and they mention in this work that the formed oxide layer is thicker for the Armco iron. The information on the oxidation behaviour of stainless steels in liquid lead-bismuth is very scarce. However, it is accepted than the available information on stainless steels oxidation in molten lead can be useful to analyse the materials behaviour in lead-bismuth. 406
For high oxygen activity, alloys with a high chromium content present a better behaviour than low chromium alloys. This is due to the different characteristics of the protective oxide layer based on formation of oxide rich in chromium, which is hindered for the low chromium alloys. At the same time, free and low chromium alloys are able to form thicker oxide layers, which are accepted to be less protective [14]. For low oxygen activity in the melt, alloys with low chromium content present a higher corrosion resistance [4], since chromium has a higher solubility than iron in lead-bismuth. This seems to be the case of Q, R (2¼ Cr-Mo) specimens comparatively to B, C (F82H) specimens although the behaviour of both steels is not conclusively different. Fedirko et al. [8] also found that spinel rich in chromium can protect iron-chromium alloys in molten lead. After 1 000 hours of testing, four different zones could be observed on the transverse micro-sections of Fe-16Cr-1Al. The first zone was a porous oxide layer with a high concentration of iron and lead and a low concentration of chromium and aluminium. This zone was formed by magnetite and lead. Lead concentration decreased with distance from the surface, but on the interface of the first and the second zone lead was present. The second zone was a continuous oxide film enriched with chromium and aluminium. The composition of this film was a Fe 3 O 4 -FeCr 2 O 4 solid solution with the spinel structure. Lead was not present in the interface between the second and third zone. A process of internal oxidation with chromium and aluminium oxides mainly along grain boundaries was detected in the third zone. Finally, the fourth zone had the matrix composition but grain boundaries also contained oxide compounds. On the contrary to the observed in oxygen saturated melts, spinel rich in chromium is not permeable to lead in solutions with low oxygen activity. In addition, in static tests performed in oxygen saturated molten lead at 520ºC, Benamati et al. [9] observed the formation of continuous layers of reaction products with an average thickness of 20 µm after 2 000 hours and of 40 µm after 3 700 hours in martensitic steel F82H mod. specimens. The reaction product layers were formed by two distinct sub-layers of Me 3 O 4 . Only the inner one contained chromium in addition to iron. Lead was detected in the outer sub-layer of all the product layers. These authors point out that oxide layers formed in oxygen saturated liquid lead containing an additional source of oxygen in the form of lead oxide are not protective, since the oxide layer thickness increases along with the exposure time. On the other hand, Müller et al. [10] found oxide layers of similar characteristics to the observed in type A specimens in samples of a martensitic steel with 9.99 Cr (OPTIFER) tested in stagnant liquid lead at 550ºC under controlled Ar-H 2 /H 2 O atmosphere containing 8 × 10 –6 at% oxygen. Müller observed a corrosion attack with three different zones. The outer layer consisted of magnetite without appreciable chromium concentration. The middle layer was formed by Cr-Fe spinel, with a chromium concentration lower than the detected in the A 3 specimens. Finally, an internal oxygen diffusion zone in which oxides precipitate along the grain boundaries could be observed. After 3 000 hours, the thickness of magnetite and spinel were 20 and 15 µm respectively whereas the depth of diffusion zone was 10 µm. According to Fedirko et al. [7], in liquid lead with low activity of oxygen the formation of the external oxide layer based on Fe 3 O 4 is very low and significant amounts of active alloying elements are accumulated in more internal layers. The lack of mobility of chromium through the magnetite lattice explains the formation of the spinel layer. Faster diffusing elements like manganese and iron will pass through to the outer layer, while slower diffusing elements like chromium will be oxidised without movement and remain in the inner layer. Both magnetite and spinels M 3 O 4 are based in a close-packed cubic sub-lattice of oxygen ions in which the metals ions are the faster moving species and determine the oxidation rates. Thus, in martensitic steels, chromium moves more slowly than iron. The outer layer is formed by magnetite and the inner layer consists of iron, chromium spinels. The 407
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Nuclear Development ACTINIDE AND FI
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FOREWORD The objective of the OECD/
Page 5 and 6:
TABLE OF CONTENTS Foreword ........
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EXECUTIVE SUMMARY More than 160 par
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identified. In the fuel area, labor
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17:20-19:05 Session III: Partitioni
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Poster sessions Poster session: Par
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WELCOME ADDRESS Lucila Izquierdo Ge
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WELCOME ADDRESS Michel Hugon Co-ord
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WELCOME ADDRESS Philippe Savelli De
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developments. This will surely beco
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use of FBRs for transmutation toget
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view, i.e. better use of uranium an
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W. Forsberg proposes to reduce the
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1. From the open fuel cycle to the
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Figures 2 and 3 show the radiotoxic
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Denoting the transuranic (TRU) or m
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or, in terms of the fuel burn-up an
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quantities of LWR-MOX and FR-MOX wi
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view of the historic development, t
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Table 5. Assumptions for transmutat
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separating troublesome fission prod
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REFERENCES [1] L.H. Baetslé, Ch. D
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SESSION III Partitioning Chairs: J.
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OVERVIEW OF THE HYDROMETALLURGICAL
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2.1.3 Consequences Owing to the fac
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The extraction and separation mecha
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extractant was observed. As a conse
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2.3.2 Examples of strategies and
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3. Conclusions and perspectives 3.1
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SESSION IV Basic Physics, Materials
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TRANSMUTATION: A DECADE OF REVIVAL
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2.1 The IFR concept and the homogen
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2.3 Dedicated systems Making again
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compound “macro-dispersed” in M
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Figure 3. Sketch of ADS, liquid met
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3.3.2.1 The MEGAPIE project [40] ME
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3.3.2.2 The MUSE experiments The MU
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Figure 8. Comparison of the neutron
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Figure 9. Scenarios at equilibrium
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goals in this field. Since once-thr
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• The use of Thorium in PWRs alwa
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• Understanding of the role of AD
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[17] Y. Arai, T. Ogawa, Research on
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SESSION V Transmutation Systems and
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1. Introduction The term ADS compre
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• Safety should be “designed in
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3. Minor actinide and/or transurani
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Table 2. Values of Dj (neutron cons
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Table 4. Delayed neutron fraction I
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Figure 4. η (Neutrons released per
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Table 5. ADS Distinguishing feature
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While a favourable ADS safety featu
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Optimised mixes of MA and Pu can be
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Moreover, the fuel is where neutron
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REFERENCES [1] L. Van den Durpel et
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[19] D.C. Wade and E. Fujita, Trend
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POSTER SESSION Basic Physics: Nucle
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To conclude, this poster session in
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Five other papers related to ADS co
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SESSION I OVERVIEW OF NATIONAL AND
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1. Current activities for radioacti
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3.2 Results to date and analyses of
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3.2.5.2 JNC JNC is considering the
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4.6 Short-term increase in radiatio
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Annex 1 R&D scheme for partitioning
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Annex 3 Members of the Advisory Com
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plutonium can be recycled in pressu
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choices and the implementation of m
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1. Introduction Since the 5th Infor
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strata” approach which would invo
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IAEA ACTIVITIES IN THE AREA OF EMER
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actually started to do so) because
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establishment of an international R
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The accelerator driven transmutatio
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substantiate this recommendation, s
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current, advanced and innovative nu
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ACCELERATOR DRIVEN SUB-CRITICAL SYS
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demonstration of feasibility of a E
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An extended “skeleton” for ADS
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• Fertile support (uranium) is no
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7. Conclusions The TWG under the ch
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1. Introduction The priorities for
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In the EURATOM Fourth Framework Pro
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Table 2. Cluster on transmutation-t
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6. Community research for the perio
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REFERENCES [1] “Council Decision
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1. Introduction Back in 1989, the O
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would need the continuation of tech
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individual isotopes as a function o
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Therefore, while there is continuin
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[9] OECD/NEA, Overview of Physics A
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RECENT TOPICS IN R&D FOR THE OMEGA
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Figure 1. Partitioning and transmut
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The present 4-GPP necessitates a pr
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5. Concluding remarks In 1999, the
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REFERENCES [1] T. Mukaiyama, T. Tak
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1. Introduction CIEMAT is actively
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adiotoxicity to be managed could al
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Figure 3. Mass composition of the d
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Figure 6. Fuel cycle assumed in the
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the 4 batches scheme, allowing to a
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Figure 11. Transmutation efficiency
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1. Introduction Spent fuels of mode
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Figure 3. A change in radiotoxicity
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These dependencies are shown on Fig
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When increasing the moderator fract
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Even greater power increases are ob
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The effect of a moderator volume fr
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Table 11. Different isotopes contri
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Thus the transmutation of such FPs
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ASSESSMENT OF NUCLEAR POWER SCENARI
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elease probabilities. The time dist
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Table 2. Annual heavy nuclide contr
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Figure 3. Reduction of potential ra
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DISPOSAL OF PARTITIONING-TRANSMUTAT
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Figure 2. Decay heat from SNF 2000
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Figure 3. Shorter-lived HHR reposit
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4. Management of low-heat, long-liv
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isotope from other caesium isotopes
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THE AMSTER CONCEPT J. Vergnes 1 , D
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Figure 1. Layout diagram of the mol
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Table 1. Definition of configuratio
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We therefore adopted a partial purg
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conceivable. Thus by increasing the
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6. R&D needed to validate the AMSTE
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SESSION III PARTITIONING J.P. Glatz
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PARTITIONING-SEPARATION OF METAL IO
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The terpyridyl reagent (ligand L 1
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Figure 2. The synthesis of ADTPTZ a
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2.4 Implications for partitioning T
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SEPARATION OF MINOR ACTINIDES FROM
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installed in a hot cell. The feed w
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the concentrations of U, Pu and Np
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Table 2 shows the recovery in the r
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PARTITIONING ANIONIC AGENTS BASED O
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which of these, the Co 3+ , Fe 3+ a
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This dianionic species must be extr
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Figure 6 Ph 2 P acetone PPh 2 H2 O
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Figure 9 H 3 C RO(CH 2 )n CH 3 (CH
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[7] J. Rais and P. Selucky, Nucleon
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PYROCHEMICAL PROCESSING OF IRRADIAT
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The metallic cadmium product of the
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Figure 2. Schematic flow-sheet for
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R&D OF PYROCHEMICAL PARTITIONING IN
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(first of all pumps) for fluoride m
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4. Research on material and equipme
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REFERENCES [1] Uhlir J., Pyrochemic
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1. Introduction The increasing inte
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Figure 2. Stainless steel box with
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Figure 4. U deposit on solid cathod
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Figure 7. Schematic flow of the cou
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actinide elements from spent (metal
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DEVELOPMENT OF PLUTONIUM RECOVERY P
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uranium dendrite and that uranium c
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Table 1. Conditions and results of
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Cathode potential went down to -1.6
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Figure 6. Change of LCC potential i
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Figure 9. Relation between Pu conce
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consideration described in the prec
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[13] Y. Arai, S. Fukushima, K. Shio
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SESSION IV BASIC PHYSICS, MATERIALS
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1. Introduction The reduction of th
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agrees ours within limits of errors
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Figure 1. Thermal neutron capture c
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[18] A.P. Baerg, R.M. Bartholomew,
Page 356 and 357: 1. Introduction Nowadays it is well
Page 358 and 359: In order to describe the inter-nucl
Page 360 and 361: kind of measurements allow to chara
Page 362 and 363: Figure 6. Two-dimensional cluster p
Page 364 and 365: Figure 8. Excitation functions for
Page 366 and 367: REFERENCES [1] D. Ridikas, thesis,
Page 368 and 369: 1. Introduction Since 1991, the Com
Page 370 and 371: Experimental reactivity control tec
Page 372 and 373: Table 2. Neutron intensities Target
Page 374 and 375: experimental channels (horizontal a
Page 376 and 377: 376
Page 378 and 379: Table 3. Planned experimental progr
Page 380 and 381: 1. Introduction and benchmark speci
Page 382 and 383: neutrons. Since the neutron flux is
Page 384 and 385: Figure 2. Microscopic capture cross
Page 386 and 387: Figure 4. k eff variation in the st
Page 388 and 389: 2.4 Neutron flux distribution One r
Page 390 and 391: etween the highest and the lowest v
Page 392 and 393: The isotope specific β eff values
Page 395: SESSION IV BASIC PHYSICS, MATERIALS
Page 398 and 399: 1. Introduction Due to its excellen
Page 400 and 401: Figure 2. Tests scheme 0 340 h. 1 0
Page 402 and 403: Figure 4. Auger depth profile conce
Page 404 and 405: Figure 8. Auger depth profile conce
Page 408 and 409: inner layer grows inward from the o
Page 410 and 411: [8] V.M. Fedirko, O.I. Eliseeva, V.
Page 412 and 413: 1. Introduction One of the main par
Page 414 and 415: 3. Tantalum target irradiation The
Page 416 and 417: At 10-MeV neutron irradiation, radi
Page 418 and 419: 1. Introduction HYPER (HYbrid Power
Page 420 and 421: this study, we used an orthogonal c
Page 422 and 423: Figure 5. Temperature distribution
Page 424 and 425: Figure 7. Thermal stress distributi
Page 427 and 428: FUEL/TARGET CONCEPTS FOR TRANSMUTAT
Page 429 and 430: (U 0.55 Pu 0.4 Np 0.05 )O 2 fuels w
Page 431 and 432: Figure 3. Left: Ceramograph of a (Z
Page 433 and 434: Figure 6. Left: ceramograph of a(Zr
Page 435 and 436: AMERICIUM TARGETS IN FAST REACTORS
Page 437 and 438: The reference case for all comparis
Page 439 and 440: It should be underlined that this c
Page 441 and 442: Cases Table 3. Heterogeneous recycl
Page 443 and 444: • A later step could be to add Cm
Page 445 and 446: RESEARCH ON NITRIDE FUEL AND PYROCH
Page 447 and 448: temperature for (Cm,Pu)N followed t
Page 449 and 450: Figure 1. Temperature dependence of
Page 451 and 452: The difference of two fuel pins exi
Page 453 and 454: In addition to the voltammetric stu
Page 455 and 456: 2 wt% of Pu at 773 K. For the momen
Page 457:
[13] M. Akabori, M. Takano, A. Itoh
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1. Introduction For the management
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The scientific feasibility of pluto
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Another option using a basis of sta
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6.2.1 Inert matrices 6.2.1.1 MgAl 2
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eached respectively 38.5% and 70% F
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Figure 4. Experiments for MA transm
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Figure 5a. Ecrix B rig Figure 5b. E
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A CEA/Minatom work programme is und
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9.3 Programme for dedicated fuels F
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[14] R.J.M. Konings et al., The EFT
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1. Introduction An accelerator driv
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corresponding Pb-Bi velocity is 1.1
Page 484 and 485:
the fission product target. The rod
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fuel rods are at the TRU assembly t
Page 489:
SESSION V TRANSMUTATION SYSTEMS AND
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1. Introduction Since the 50s, nitr
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A three dimensional model of a sub-
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Figure 4. Change in k-eigenvalue fo
Page 498 and 499:
[4] Y. Arai et al., Experimental Re
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Nomenclature ADS: ATW: GT-MHR: LOF:
Page 502 and 503:
Regarding switching off the beam, o
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Figure 3. Beam blocking 10 min (200
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Figure 7. A possible scenario for n
Page 508 and 509:
[15] Greenspan E. et al., The Encap
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1. Introduction In the EADF design
Page 512 and 513:
Equation (6) can be improved by con
Page 514 and 515:
where L is obtained by a summation
Page 516 and 517:
Figure 1. The natural convection im
Page 518 and 519:
Figure 4 shows the temperature tren
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[12] P.H. Wakker, Thermal Hydraulic
Page 522 and 523:
1. Introduction Research and develo
Page 524 and 525:
Table 2. Core design parameters for
Page 526 and 527:
2.2 Representation of MA transmutat
Page 528 and 529:
Figure 1(b) shows the cases for the
Page 530 and 531:
It is found that the higher MA tran
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REFERENCES [1] T. Ikegami, H. Hayas
Page 534 and 535:
1. Introduction The management of t
Page 536 and 537:
Table 1. Core performance of MA and
Page 538 and 539:
Figure 3. Nuclear electricity capac
Page 540 and 541:
Table 3. Experimental items at PEF
Page 542 and 543:
REFERENCES [1] Takano H., Akie H.,
Page 544 and 545:
1. Introduction and background The
Page 546 and 547:
neutron source, the reactor can mai
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atoms. For fuel region Rf = 2.5 cm,
Page 550 and 551:
Figure 3. Neutron flux spectra for
Page 552 and 553:
A possible way to maintain the k ef
Page 554 and 555:
higher than 99% of 239 Pu, and high
Page 557 and 558:
TRANSMUTATION OF NUCLEAR WASTES WIT
Page 559 and 560:
Figure 1. PBT conceptual view Table
Page 561 and 562:
very tight holders for fission frag
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5. Cooling system A preliminary des
Page 565 and 566:
spectral densities [10,11] and can
Page 567 and 568:
MYRRHA, A MULTI-PURPOSE ADS FOR R&D
Page 569 and 570:
hexagonal assemblies of 122 mm plat
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to achieve the requested performanc
Page 573 and 574:
3 MYRRHA associated R&D programme F
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collaboration with Forschungszentru
Page 577:
• Industrial partners, in particu
Page 580 and 581:
1. Introduction The transmutation o
Page 582 and 583:
Existing accelerators have been des
Page 584 and 585:
suggested to look for an innovative
Page 586 and 587:
Table 1. Main lead-bismuth eutectic
Page 588 and 589:
4.3 The core The basic fuel sub-ass
Page 590 and 591:
Figure 1. Experimental accelerator
Page 593 and 594:
HELIUM-COOLED REACTOR TECHNOLOGIES
Page 595 and 596:
of its potential use in nuclear wea
Page 597 and 598:
Figure 2. Neutron flux distribution
Page 599 and 600:
atio. Given this rate of destructio
Page 601 and 602:
Figure 5. Irradiated TRISO particle
Page 603 and 604:
in ceramic-coated microspheres of t
Page 605 and 606:
(LOCA) event. The effect on this fe
Page 607 and 608:
Figure 13. Elevation AD-FMHR The fa
Page 609:
Deep burn-up of 239 Pu and fissiona
Page 613:
POSTER SESSION PARTITIONING M.J. Hu
Page 616 and 617:
1. Introduction The study of the be
Page 618 and 619:
Plutonium was simulated with the no
Page 620 and 621:
The influence of uranium and pluton
Page 622 and 623:
The influence of uranium and pluton
Page 624 and 625:
REFERENCES [1] I.I. Nazarenko, A.M.
Page 626 and 627:
1. Introduction The long-term radio
Page 628 and 629:
Ce Ce 3+ Cl - Cl 2 The voltammogram
Page 630 and 631:
Figure 3. Chronopotentiograms for t
Page 632 and 633:
Figure 4. Potentiometric titrations
Page 634 and 635:
Experimental solubilization tests w
Page 636 and 637:
[13] H. Flood T. Förland and K. Mo
Page 638 and 639:
1. Introduction The separation of l
Page 640 and 641:
Figure 4. Synthesis of amides 11-15
Page 642 and 643:
1. Introduction Over the recent yea
Page 644 and 645:
2.3.2 Set-up We set up a single HFM
Page 646 and 647:
lower flow rates, Am(III) would be
Page 649 and 650:
THE POTENTIAL OF NANO- AND MICROPAR
Page 651 and 652:
efficiently and stable. This can be
Page 653 and 654:
Figure 1a. Zetapotential of NTA-mod
Page 655 and 656:
Scheme 7. Magnetic silica particles
Page 657:
[13] L.H. Delmau, N. Simon, M.J. Sc
Page 660 and 661:
1. Introduction 137 90 Extraction p
Page 662 and 663:
Figure 3. Schematic drawing of the
Page 664 and 665:
(24), 8-PhPO(OH)-O-COSAN (25), and
Page 666 and 667:
REFERENCES [1] Kyrš M., +H PiQHN S
Page 668 and 669:
1. Introduction A heavy-water CANDU
Page 670 and 671:
These data show that fuel lifetime
Page 673 and 674:
RECENT PROGRESSES ON PARTITIONING S
Page 675 and 676:
hot tests (See Table2) was enough f
Page 677 and 678:
trace amount of Am and Eu. The HBTM
Page 679 and 680:
6. Conclusion Declassification of t
Page 681:
POSTER SESSION BASIC PHYSICS: NUCLE
Page 684 and 685:
1. Introduction Among the large num
Page 686 and 687:
The simulation of the spallation pr
Page 688 and 689:
Table 1. Parameters of the two coll
Page 690 and 691:
Figure 4. Radial distribution of th
Page 692 and 693:
6. The neutron escape line The comm
Page 694 and 695:
Figure 7. Neutron background at the
Page 697 and 698:
RECENT CAPTURE CROSS-SECTIONS VALID
Page 699 and 700:
Figure 1. The GENEPI accelerator an
Page 701 and 702:
2.3.3 Neutron flux measurements •
Page 703 and 704:
Figure 6. Time spectrum of 3 He gas
Page 705 and 706:
4. Analysis 4.1 Background subtract
Page 707 and 708:
Figure 11. ENDF/B-VI, JEF2.2 and JE
Page 709 and 710:
DOUBLE DIFFERENTIAL CROSS-SECTION F
Page 711 and 712:
3. Conclusion Double differential c
Page 713 and 714:
Figure 3. Preliminary results of do
Page 715 and 716:
MEASUREMENTS OF PARTICULE EMISSION
Page 717 and 718:
2. Experimental set-up The experime
Page 719:
4. Results Figure 3 presents neutro
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1. Introduction Intermediate-energy
Page 724 and 725:
Table 1. Relative neutron-induced c
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elow about 70 MeV [24] , where σ n
Page 728 and 729:
Since for sub-actinides Γ f /Γ n
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[10] V.P. Eismont, A.V. Prokofiev,
Page 733 and 734:
NUCLEON-INDUCED FISSION CROSS-SECTI
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Figure 1. Scheme of the new code Z
Page 737 and 738:
Figure 3. Neutron-induced fission c
Page 739:
REFERENCES [1] J. Raynal, Proceedin
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1. Introduction During the past few
Page 744 and 745:
(same surface and 0.5 mm thickness)
Page 746 and 747:
Figure 2. Dependence of the total a
Page 748 and 749:
Figure 3. Neutron radiative capture
Page 750 and 751:
[8] MCNP, A General Monte Carlo Cod
Page 752 and 753:
1. Introduction New reactors using
Page 754 and 755:
Figure 1. Excited states of 209 Bi
Page 756 and 757:
Figure 3. The fission probability o
Page 759 and 760:
MEASUREMENT OF DOUBLE DIFFERENTIAL
Page 761 and 762:
Figure 1. Global view of the experi
Page 763 and 764:
To get the proton (deuteron) energy
Page 765 and 766:
3.1 Corrections Several corrections
Page 767 and 768:
Figure 11. Active target fraction (
Page 769 and 770:
d 2 σ Figure 14. Proton for n + Pb
Page 771 and 772:
HIGH AND INTERMEDIATE ENERGY NUCLEA
Page 773 and 774:
eactions, since the pre-equilibrium
Page 775 and 776:
calculate the very short-lived radi
Page 777 and 778:
cross-sections; the secondary react
Page 779 and 780:
All possible nuclear reactions will
Page 781 and 782:
A STUDY ON BURNABLE ABSORBER FOR A
Page 783 and 784:
2. Burnable absorber for HYPER 2.1
Page 785 and 786:
Table 2. One-group effective cross-
Page 787 and 788:
of the core, is directly determined
Page 789 and 790:
Figure 4. Required proton beam curr
Page 791 and 792:
Figure 8. 10 B depletion in HYPER-H
Page 793:
POSTER SESSION TRANSMUTATION SYSTEM
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1. Introduction In the framework of
Page 798 and 799:
Φ >1 MeV = 1.0 10 13 to 1.0 x 10 1
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3. Irradiation targets and irradiat
Page 802 and 803:
e transmuted in BR2 hence remain va
Page 804 and 805:
Table 6. Atom percent concentration
Page 806 and 807:
advantage, with respect to FRs, of
Page 809 and 810:
ENHANCEMENT OF ACTINIDE INCINERATIO
Page 811 and 812:
Here Σ fC , ( E) are the fission a
Page 813 and 814:
pellet and the steel cladding. In o
Page 815 and 816:
Table 3.Neutronics parameters of hy
Page 817 and 818:
Figure 3. Neutron spectra averaged
Page 819 and 820:
containing FA with B 4 C cladding i
Page 821:
REFERENCES [1] ANSALDO Technical Re
Page 824 and 825:
1. Introduction At present, there a
Page 826 and 827:
target means a change in k and the
Page 828 and 829:
Following the normal procedure for
Page 830 and 831:
Acknowledgements This study has bee
Page 832 and 833:
1. ADS description A conceptual des
Page 834 and 835:
Substitution of (9) into (8), and u
Page 836 and 837:
With the coupling LAHET + MCNP-DSP,
Page 838 and 839:
Figure 3. Comparison for 1 and 5 pu
Page 841 and 842:
MOLTEN SALTS AS POSSIBLE FUEL FLUID
Page 843 and 844:
2. The fuel salt for MSB concept Ma
Page 845 and 846:
and minor actinides must be removed
Page 847 and 848:
4. Container material studies 4.1 F
Page 849 and 850:
management. The major developments
Page 851:
REFERENCES [1] H.J. MacPherson, Dev
Page 854 and 855:
1. Introduction The Energy Amplifie
Page 856 and 857:
Table 1. Main parameters of the EAD
Page 858 and 859:
Table 5. Neutron balance in the who
Page 860 and 861:
Table 7. Neutron flux distributions
Page 862 and 863:
Table 8. Displacement rates DPA/yea
Page 865 and 866:
DEEP UNDERGROUND TRANSMUTOR (PASSIV
Page 867 and 868:
passive state. By operating at a hi
Page 869 and 870:
I have proposed using an accelerato
Page 871 and 872:
Figure 1. Layout of deep undergroun
Page 873 and 874:
RADIATION CHARACTERISTICS OF PWR MO
Page 875 and 876:
Table 1. Radiotoxicity of actinides
Page 877 and 878:
RADIATION CHARACTERISTICS OF URANIU
Page 879 and 880:
Table 1. Radiotoxicity of actinides
Page 881 and 882:
INTERNATIONAL CO-OPERATION ON CREAT
Page 883 and 884:
an international base to combine ef
Page 885:
• Second topic: interaction of pr
Page 888 and 889:
1. Introduction The role of acceler
Page 890 and 891:
MEPI within the framework of Projec
Page 893 and 894:
NEW ORIGINAL IDEAS ON ACCELERATOR D
Page 895 and 896:
During conceptual investigations of
Page 897 and 898:
delay, interface and computer. The
Page 899 and 900:
2. Channel-vessel design of ADS bla
Page 901 and 902:
Table 1. Characteristics of the ful
Page 903:
[14] Karavaev G.N., Kiselev G.V., M
Page 906 and 907:
1. Introduction The problem of nucl
Page 908 and 909:
Table 3. Radiotoxicity in americium
Page 910 and 911:
Table 5. Characteristics of station
Page 912 and 913:
1. Introduction The atomic power en
Page 914 and 915:
of lead-bismuth target are given in
Page 917 and 918:
CRITICAL AND SUB-CRITICAL GT-MHRs F
Page 919 and 920:
Table 1. Basic GT-MHR reactor param
Page 921 and 922:
Figure 2. Typical change of the ave
Page 923 and 924:
Scenario S4. This case is actually
Page 925 and 926:
Figure 3. A change in radiotoxicity
Page 927:
[13] P. Goberis, Modelling of Innov
Page 930 and 931:
1. Introduction The Nuclear Enginee
Page 932 and 933:
Some simplifications have been made
Page 934 and 935:
Figure 3. Velocity vectors Some of
Page 936 and 937:
Figure 6. Temperature evolution at
Page 938 and 939:
• Two main reasons can explain th
Page 940 and 941:
1. Introduction Actually, we notice
Page 942 and 943:
This problem can be solved by using
Page 944 and 945:
The evaluations obtained in [2] hav
Page 946 and 947:
REFERENCES [1] Management and Dispo
Page 948 and 949:
1. Background Radiation background
Page 950 and 951:
the long-term hazard of spent fuel,
Page 952 and 953:
In a transmutation fuel cycle inclu
Page 954 and 955:
Figure 4. Potential biological haza
Page 956 and 957:
cooling prior to SF reprocessing an
Page 958:
REFERENCES [1] White Book of Nuclea
Page 961 and 962:
ORDER FORM OECD Nuclear Energy Agen
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