CA1211344A - Method of manufacturing cladding tubes of a zirconium- based alloy for fuel rods for nuclear reactors - Google Patents
Method of manufacturing cladding tubes of a zirconium- based alloy for fuel rods for nuclear reactorsInfo
- Publication number
- CA1211344A CA1211344A CA000406695A CA406695A CA1211344A CA 1211344 A CA1211344 A CA 1211344A CA 000406695 A CA000406695 A CA 000406695A CA 406695 A CA406695 A CA 406695A CA 1211344 A CA1211344 A CA 1211344A
- Authority
- CA
- Canada
- Prior art keywords
- zirconium
- temperature
- based alloy
- quenching
- cold rolling
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired
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Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
- C22F1/18—High-melting or refractory metals or alloys based thereon
- C22F1/186—High-melting or refractory metals or alloys based thereon of zirconium or alloys based thereon
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- Chemical & Material Sciences (AREA)
- Mechanical Engineering (AREA)
- Organic Chemistry (AREA)
- Crystallography & Structural Chemistry (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Physics & Mathematics (AREA)
- Metallurgy (AREA)
- Thermal Sciences (AREA)
- Powder Metallurgy (AREA)
- Heat Treatment Of Nonferrous Metals Or Alloys (AREA)
- Heat Treatment Of Steel (AREA)
- Extrusion Of Metal (AREA)
- Metal Extraction Processes (AREA)
- Pressure Welding/Diffusion-Bonding (AREA)
Abstract
ABSTRACT
In the manufacture of cladding tubes of a zirconium-based alloy for fuel rods for nuclear reactors by extrusion of the zirconium-based alloy and cold rollings of the extruded product with anneal-ings, intermediate annealings, between the cold rollings and a .beta.-quenching prior to the last cold rolling, a cladding tube is provided which has at the same time good corrosion properties and mechanical properties by performing the .beta.-quenching prior to a cold rolling, after which an intermediate annealing is performed at a temperature of 500-675 °C, and preferably at a temperature of 500-610 °C.
!
In the manufacture of cladding tubes of a zirconium-based alloy for fuel rods for nuclear reactors by extrusion of the zirconium-based alloy and cold rollings of the extruded product with anneal-ings, intermediate annealings, between the cold rollings and a .beta.-quenching prior to the last cold rolling, a cladding tube is provided which has at the same time good corrosion properties and mechanical properties by performing the .beta.-quenching prior to a cold rolling, after which an intermediate annealing is performed at a temperature of 500-675 °C, and preferably at a temperature of 500-610 °C.
!
Description
~N c995 3 ~ ~
A method of manufacturing cladding tubes of a zirconium-based ~lloy for The present invention relate6 to a method for manufacturing cladding tube~
of a ~irconium-based alloy for fuel rods for nuclear rsactors.
As cladding tubes for ~uel rods for nuclear reactors there are normally used thin-walled tube~ of zirconium-baeed alloy~, known under the n~me ZircaloyJ The~e alloy3 contain alloying materials such as tin, iron and nickel. In Zircaloy the ~-pha~e i8 ~table below 79O C, the ~ -phaae i8 stable above 9~O C, whereas a two-phase re~ion, the C~ -phase region, OCCUr9 between 79O C and 95O C. In the G~-pha~e the zirConiUm atoms are arranged in a hexagonal close packed lattice and in the ~ -phase in a body centered ~ubic lattioeO During so-called ~ -quenching of Zir~aloy*to bring abo~the de~ired properties 0ùch a3 improved oorro~lon properties of ~he ~aterial9 the material 9 heated to a temperature in the ~ -pha~e region and rapidly : oooled to a temperature in the ~ pha~e region~
During conventional manufacture of cladding tubes o~ Zircaloyi a ~ quenching of the ~aterial i~ performed after forging of i~got3 into rods, ~fter the.
~anufacture o~ extrusion billets of the rods; the billets ~re extxuded in the phase region at a temperature of 680 C, wherea~ter the e~truded product iB
subjected to cold rollings in a ~u~ber o~ 8tep8 and, between two o~eGuti~e co * A Trademark - i ,,, ,- .
, . .....
~2~3~
rollings, an annealing, intermediate annealing, at 625-700 C to enable the subsequent cold rolling. After the last cold rolling step, a final annealing is performed to give the material the desired properties. ~he final annealing may be ~erformed at temperatures of 400-700 C.
Tubes manufactured from Zircaloy under the conditions uæed so far have generally proved to posses3 sufficient resistance to corrosion under the operating conditions prevailing in a nuclear reactor. ~o~rever7 the develop-ment proceeds towards an increasingly higher utilization of the fuel7 which means longer operating times for the fuel assemblies. qhe claddin~ material will therefore be subjected to the corrosive water for a longer perioB of time than what ha~ been normal previously, which results in an increased risk of corrosion damage. It has therefore been a desire to achieve better corrosion properties in the alloys used without thi~ in~olving unfavourable changes of the mechanical properties.
.~
It is previously known9 among other things from the U,S. patent specific~-tion 4,238,251, that by ~-quenching of a finished tube of Zircaloy it is possible to improve the resistance of the tube to so-called accelerated nodular corro~ion in water and steam of high pressure As will be ¢lear from U.S. patent specification ~,~65,635, tubes of Zixcaloy having good mechanical properties may be achieved by ~-quenching of the extruded product before this is subjected to the final cold rolling operation.
The exact reason for the improved resistance to accelerated nodular corrosion achieved by ~ quenching has as yet not been completely established. It i8 considered, however, that the improvement is related to the ~ize and distri-bution of the intermetallic compounds in the material~ ~he intermetallic compounds, so-~alled second phases, consist of ¢hemical compounds containing, beside~ zirconium, primarily the èlements iron~chromium and nickel and they exist in the form of particles~ The dissolution and preGipitation process a¢complished by the ~ quenching results in a reduction of the size of the particles as well a~ in a redistributio~ from evenly distributed particle~
to particles constituting arrays at the grain boundaries of the ~-grain~
formed during the ~ phase transformation.
A ~quenching of the finished cladding tube results in a reduction of the ductility of the tube, which involve~ ~ disadvantago with the method. A ~-quenching of the extruded product prior to cold rolling into the final dimension ~Z~L3~
gives leg9 deterioratio~ of the mechanioal propertie8 of the finished tube.
quenching, however, regardles~ of whether it takes place on a finished tube or prior to the final cold rolling step, results in an impaired yield because of the increa~ed ~mount of aCrap and further beGause Or material losses since a ~quenchin6 leads to the formation of an oxide la~er on the surface of the tube, which mu~t be removed.
i Acoording to the present invention, it has proved to be po3sible to manufac-ture cladding/for ~uel rods for nuclear reactors ha~ing at leaat as good re~istance ~o nodular corrosion ao the be~t previously known cladding tube6 and at the sam~ time a better ductility than such cladding tubes. Compared with previously known method3 of manufacturing cladding tubes while using ~ _ ~uenching after the extrusion, u~in~ the present invention, which also in-cludes ~ quenching, results in an improved yield because of reduced s¢rap and further reduced material losseR since the oxides form2d can be re~.oved on a smaller surface by performing the ~-quenching in an earlierstage of the manufacturin~ process.
~he invention relates to a method of manufacturin~ a cladding tube of a zirconium-based alloy for fuel rod~ for nuclear reactors, the zirconium-based allo~ being extruded and the extruded product bsing subjected to cold rolling~ and at least one annealing, intermediate annealing, between two consecutive cold rollings and a ~^luenching prior to the final oold rolling, characterised in that the ~ quenching is performed prior to a cold rolling, after which at least one intermediate annealing is pex~ormed at a temperature of 500-675 C. The preferred temperature for the in~ermediate annealing is 500-6~10 C, and the specially preferred temperature is 550-600 C.
The extrusion ¢an be carried out at sn arbitra~y temperature in the c~-Pha80 region~ !
After the last cold rolling, the extruded product is subjected to a final annealing at a temperature o~ ~400~675 GC ~ preferably at a tenlperature of 400-610 C and especially preferably at a temperature of 550-~he ~-quenching of the extruded product i~ carried out by heatLng the product to a temperature in the ~ phase region, suîtably to a temperature of 950-1250 Cand preferably to a tempexature of 1000-1150 C and thereafter rapidly oooling it to a temperature in the o~_phase region. ~he cooling from the temperature used in the ~-phase xegion to the temperature 790 C then guitably takes place a-t a rate of 20-400 C per second and the cooling from 790 C to 500 C or a temperature therebslow suitably at a rate of more than 5 C per minute.
In the manufacture of cladding tubes according to the present invention, it has pro~ed that the size of the second phase particles in the finished cladding tube, as in the case where ~ uenching i~ u~ed, is considerably smaller than with conventional manufacture of oladding tu~es ~lithout ~ -quenching after the extrusion. Ho~lever, contrary to what i8 the caae after ~ -quenching in previously known methods, the second phase particles are homo-geneously distributed in the material. It i9 pos~ible that it i9 the small size of the second pha~e particles achieved according to the present invention, together with the homogeneous distribution thereof, which gives the fa~ourable combination of good resistance to nodular corrosion and good mechanical properties.
The zirconium~ba~ed alloy preferably consists of a zirconium-tin alloy, for example the alloy~ known under the trade name~ Zircaloy 2 and Zircaloy 4, whose contents of alloying material lie within the l;m;ts 1.2-1.7 ~ for tin, 0.07-0 24 % for iron, 0005-0.15 % for chromium and 0-0,08 % for nickel, the balance being zirconium and any existing Lmpurities of ordinary kind, the percentages stated, as well as other percentages stated in the application, referring to percentage by weight. Zircaloy 2 contains 1.2-1.7 ~0 tin, 0.07-0.20 ~ iron, 0.05-0.15 % chromium,and 0.03-0.08 ~o nickel. Zircaloy 4 contains 1.2-1.7 % tin7 0.18-0.24 % iron, 0.07-0.13 % chromium and no nicXel.
The æirconium-ba~ed alloy i~ preferably subjected to a ~-quenching prior to the extrusion, that is, it i~ heated to a temperature in the ~ phase region and rapidly cooled to a temperature in the c~-phase region. ~oweverj it is possible to use the zirconium based alloy without~`it b~ing subjected to ~ -quenching. ~ -quenching prior to the extrusion i8 carried out by heating the alloy to a temperature o~ suitably 950-1250 C and of preferably 1000-1150 C
ana by rapidly coaling it to a temperature in the o~-phase region. The oooling from the u~ed temperature in the ~-phase region to the temperature 790 C then suitably takes place at a rate of 1-50 C per second and the cool-ing from 790 C to 500 C or a temperature therebelow ~uitably at a rate of more tha~ 5 C per mi~ute.
~he in~ention will be e~plained in greater detail by de~cribing an example.
An ing~t of Zircaloy 2 i~ forged into a rod with a dimension of 150-200 m~O
~he rod i8 subjected to ~ -quenching by heating it to a temperature o~ 1050 C
for 15 minutes a~d cooli~g it to room temperature at a rate of 5-10 & /~e¢ond.
~LZ~L3~
Ext~usion billets ~re made from the rod. ~hese billets are extruded at a temperature of 700 - 740 C, that iæ, in the ~ ~hase region. The extruded product iB thereafter subjected to three cold rolling operation~ whereby the final outer diameter of the tube becomes 12.~ mm. ~etween the firs-t and the second rolling the extruded product is subject0d to a ~ quenching by heating it up to 1050 C for a few seconds with a high frequency coil arTanged around it, whereafter it iæ cooled at a rate of 200 ~C/~eoond to room temperatuxe by water spraying. Between the seco~d and last rolling, the ext~uded product i3 annealed at a temperature of 575 C. After the last cold rolling, the tube is finally annealed at a temperature of 565 C, Both intermediate annealings and the final annealin~ may be carried out in an evacuated furnace. ~ In the ~inished tube, the second phase particles have a size which i8 substantially in the interval 0.05-0.4/um and a mean particle size of around 0015 ~ . In a cladding tube which has been manufactured in a conventional manner and which has not been subjected to ~-quenching in finished state or earlier in extruded state, the second phase particles have a size whichis substantially in the interval 0.1-0.6/um and a mean particle size of about 00 3/um.
During corrosion tests which have proved to simulate well the conditions in reactor operation9 cladding tube~ manufactured according to the present inventian exhibit ueight gain which i8 only a ~raction of that which is obtained in conventional manufacture without the use of ~ quenching after the extrusion and approximately as great as that obtained during manufacture while using ~quenching after the extrusion, 50-100 mg/dm2 according to the invention and 350 4000 mg/dm2 during co~ventional manufac-ture without the use of ~-quenching. ~he ductility of a cladding tube manufactured according to the invention is better than with tubes which have been sub~ected to ~uenching in finished atate and with tubes which have been subjected to ~quenching immediatel~ prior to the last cold rollin~.
Ihe above-mentioned corrosion tests are performed in an autoclave with water vapour at a pressure of 9.8 MPa and a temperature of 500 ~. The weight gain i~ a mea~ure of the corrosion to which the tube has been ~ubjeQted.
A method of manufacturing cladding tubes of a zirconium-based ~lloy for The present invention relate6 to a method for manufacturing cladding tube~
of a ~irconium-based alloy for fuel rods for nuclear rsactors.
As cladding tubes for ~uel rods for nuclear reactors there are normally used thin-walled tube~ of zirconium-baeed alloy~, known under the n~me ZircaloyJ The~e alloy3 contain alloying materials such as tin, iron and nickel. In Zircaloy the ~-pha~e i8 ~table below 79O C, the ~ -phaae i8 stable above 9~O C, whereas a two-phase re~ion, the C~ -phase region, OCCUr9 between 79O C and 95O C. In the G~-pha~e the zirConiUm atoms are arranged in a hexagonal close packed lattice and in the ~ -phase in a body centered ~ubic lattioeO During so-called ~ -quenching of Zir~aloy*to bring abo~the de~ired properties 0ùch a3 improved oorro~lon properties of ~he ~aterial9 the material 9 heated to a temperature in the ~ -pha~e region and rapidly : oooled to a temperature in the ~ pha~e region~
During conventional manufacture of cladding tubes o~ Zircaloyi a ~ quenching of the ~aterial i~ performed after forging of i~got3 into rods, ~fter the.
~anufacture o~ extrusion billets of the rods; the billets ~re extxuded in the phase region at a temperature of 680 C, wherea~ter the e~truded product iB
subjected to cold rollings in a ~u~ber o~ 8tep8 and, between two o~eGuti~e co * A Trademark - i ,,, ,- .
, . .....
~2~3~
rollings, an annealing, intermediate annealing, at 625-700 C to enable the subsequent cold rolling. After the last cold rolling step, a final annealing is performed to give the material the desired properties. ~he final annealing may be ~erformed at temperatures of 400-700 C.
Tubes manufactured from Zircaloy under the conditions uæed so far have generally proved to posses3 sufficient resistance to corrosion under the operating conditions prevailing in a nuclear reactor. ~o~rever7 the develop-ment proceeds towards an increasingly higher utilization of the fuel7 which means longer operating times for the fuel assemblies. qhe claddin~ material will therefore be subjected to the corrosive water for a longer perioB of time than what ha~ been normal previously, which results in an increased risk of corrosion damage. It has therefore been a desire to achieve better corrosion properties in the alloys used without thi~ in~olving unfavourable changes of the mechanical properties.
.~
It is previously known9 among other things from the U,S. patent specific~-tion 4,238,251, that by ~-quenching of a finished tube of Zircaloy it is possible to improve the resistance of the tube to so-called accelerated nodular corro~ion in water and steam of high pressure As will be ¢lear from U.S. patent specification ~,~65,635, tubes of Zixcaloy having good mechanical properties may be achieved by ~-quenching of the extruded product before this is subjected to the final cold rolling operation.
The exact reason for the improved resistance to accelerated nodular corrosion achieved by ~ quenching has as yet not been completely established. It i8 considered, however, that the improvement is related to the ~ize and distri-bution of the intermetallic compounds in the material~ ~he intermetallic compounds, so-~alled second phases, consist of ¢hemical compounds containing, beside~ zirconium, primarily the èlements iron~chromium and nickel and they exist in the form of particles~ The dissolution and preGipitation process a¢complished by the ~ quenching results in a reduction of the size of the particles as well a~ in a redistributio~ from evenly distributed particle~
to particles constituting arrays at the grain boundaries of the ~-grain~
formed during the ~ phase transformation.
A ~quenching of the finished cladding tube results in a reduction of the ductility of the tube, which involve~ ~ disadvantago with the method. A ~-quenching of the extruded product prior to cold rolling into the final dimension ~Z~L3~
gives leg9 deterioratio~ of the mechanioal propertie8 of the finished tube.
quenching, however, regardles~ of whether it takes place on a finished tube or prior to the final cold rolling step, results in an impaired yield because of the increa~ed ~mount of aCrap and further beGause Or material losses since a ~quenchin6 leads to the formation of an oxide la~er on the surface of the tube, which mu~t be removed.
i Acoording to the present invention, it has proved to be po3sible to manufac-ture cladding/for ~uel rods for nuclear reactors ha~ing at leaat as good re~istance ~o nodular corrosion ao the be~t previously known cladding tube6 and at the sam~ time a better ductility than such cladding tubes. Compared with previously known method3 of manufacturing cladding tubes while using ~ _ ~uenching after the extrusion, u~in~ the present invention, which also in-cludes ~ quenching, results in an improved yield because of reduced s¢rap and further reduced material losseR since the oxides form2d can be re~.oved on a smaller surface by performing the ~-quenching in an earlierstage of the manufacturin~ process.
~he invention relates to a method of manufacturin~ a cladding tube of a zirconium-based alloy for fuel rod~ for nuclear reactors, the zirconium-based allo~ being extruded and the extruded product bsing subjected to cold rolling~ and at least one annealing, intermediate annealing, between two consecutive cold rollings and a ~^luenching prior to the final oold rolling, characterised in that the ~ quenching is performed prior to a cold rolling, after which at least one intermediate annealing is pex~ormed at a temperature of 500-675 C. The preferred temperature for the in~ermediate annealing is 500-6~10 C, and the specially preferred temperature is 550-600 C.
The extrusion ¢an be carried out at sn arbitra~y temperature in the c~-Pha80 region~ !
After the last cold rolling, the extruded product is subjected to a final annealing at a temperature o~ ~400~675 GC ~ preferably at a tenlperature of 400-610 C and especially preferably at a temperature of 550-~he ~-quenching of the extruded product i~ carried out by heatLng the product to a temperature in the ~ phase region, suîtably to a temperature of 950-1250 Cand preferably to a tempexature of 1000-1150 C and thereafter rapidly oooling it to a temperature in the o~_phase region. ~he cooling from the temperature used in the ~-phase xegion to the temperature 790 C then guitably takes place a-t a rate of 20-400 C per second and the cooling from 790 C to 500 C or a temperature therebslow suitably at a rate of more than 5 C per minute.
In the manufacture of cladding tubes according to the present invention, it has pro~ed that the size of the second phase particles in the finished cladding tube, as in the case where ~ uenching i~ u~ed, is considerably smaller than with conventional manufacture of oladding tu~es ~lithout ~ -quenching after the extrusion. Ho~lever, contrary to what i8 the caae after ~ -quenching in previously known methods, the second phase particles are homo-geneously distributed in the material. It i9 pos~ible that it i9 the small size of the second pha~e particles achieved according to the present invention, together with the homogeneous distribution thereof, which gives the fa~ourable combination of good resistance to nodular corrosion and good mechanical properties.
The zirconium~ba~ed alloy preferably consists of a zirconium-tin alloy, for example the alloy~ known under the trade name~ Zircaloy 2 and Zircaloy 4, whose contents of alloying material lie within the l;m;ts 1.2-1.7 ~ for tin, 0.07-0 24 % for iron, 0005-0.15 % for chromium and 0-0,08 % for nickel, the balance being zirconium and any existing Lmpurities of ordinary kind, the percentages stated, as well as other percentages stated in the application, referring to percentage by weight. Zircaloy 2 contains 1.2-1.7 ~0 tin, 0.07-0.20 ~ iron, 0.05-0.15 % chromium,and 0.03-0.08 ~o nickel. Zircaloy 4 contains 1.2-1.7 % tin7 0.18-0.24 % iron, 0.07-0.13 % chromium and no nicXel.
The æirconium-ba~ed alloy i~ preferably subjected to a ~-quenching prior to the extrusion, that is, it i~ heated to a temperature in the ~ phase region and rapidly cooled to a temperature in the c~-phase region. ~oweverj it is possible to use the zirconium based alloy without~`it b~ing subjected to ~ -quenching. ~ -quenching prior to the extrusion i8 carried out by heating the alloy to a temperature o~ suitably 950-1250 C and of preferably 1000-1150 C
ana by rapidly coaling it to a temperature in the o~-phase region. The oooling from the u~ed temperature in the ~-phase region to the temperature 790 C then suitably takes place at a rate of 1-50 C per second and the cool-ing from 790 C to 500 C or a temperature therebelow ~uitably at a rate of more tha~ 5 C per mi~ute.
~he in~ention will be e~plained in greater detail by de~cribing an example.
An ing~t of Zircaloy 2 i~ forged into a rod with a dimension of 150-200 m~O
~he rod i8 subjected to ~ -quenching by heating it to a temperature o~ 1050 C
for 15 minutes a~d cooli~g it to room temperature at a rate of 5-10 & /~e¢ond.
~LZ~L3~
Ext~usion billets ~re made from the rod. ~hese billets are extruded at a temperature of 700 - 740 C, that iæ, in the ~ ~hase region. The extruded product iB thereafter subjected to three cold rolling operation~ whereby the final outer diameter of the tube becomes 12.~ mm. ~etween the firs-t and the second rolling the extruded product is subject0d to a ~ quenching by heating it up to 1050 C for a few seconds with a high frequency coil arTanged around it, whereafter it iæ cooled at a rate of 200 ~C/~eoond to room temperatuxe by water spraying. Between the seco~d and last rolling, the ext~uded product i3 annealed at a temperature of 575 C. After the last cold rolling, the tube is finally annealed at a temperature of 565 C, Both intermediate annealings and the final annealin~ may be carried out in an evacuated furnace. ~ In the ~inished tube, the second phase particles have a size which i8 substantially in the interval 0.05-0.4/um and a mean particle size of around 0015 ~ . In a cladding tube which has been manufactured in a conventional manner and which has not been subjected to ~-quenching in finished state or earlier in extruded state, the second phase particles have a size whichis substantially in the interval 0.1-0.6/um and a mean particle size of about 00 3/um.
During corrosion tests which have proved to simulate well the conditions in reactor operation9 cladding tube~ manufactured according to the present inventian exhibit ueight gain which i8 only a ~raction of that which is obtained in conventional manufacture without the use of ~ quenching after the extrusion and approximately as great as that obtained during manufacture while using ~quenching after the extrusion, 50-100 mg/dm2 according to the invention and 350 4000 mg/dm2 during co~ventional manufac-ture without the use of ~-quenching. ~he ductility of a cladding tube manufactured according to the invention is better than with tubes which have been sub~ected to ~uenching in finished atate and with tubes which have been subjected to ~quenching immediatel~ prior to the last cold rollin~.
Ihe above-mentioned corrosion tests are performed in an autoclave with water vapour at a pressure of 9.8 MPa and a temperature of 500 ~. The weight gain i~ a mea~ure of the corrosion to which the tube has been ~ubjeQted.
Claims (8)
1. A method of manufacturing cladding tubes of a zirconium-based alloy for fuel rods for nuclear reactors, the zirconium-based alloy being extruded and the extruded product being subjected to cold rollings and at least one annealing, intermediate annealing, between two consecutive cold rollings and one .beta.-quenching prior to the last cold rolling, characterized in that the .beta.-quenching is performed prior to a cold rolling, after which at least one intermediate annealing is performed at a temperature of 500-675°C.
2. A method according to claim 1, characterised in that the intermediate annealing is performed at a temperature of 500-610°C.
3. A method according to claim 1 characterised in that the zirconium-based alloy contains 1.2-1.7 per cent by weight tin, 0.07-0.24 per cent by weight iron, 0.05-0.15 per cent by weight chromium and 0-0.08 per cent by weight nickel, the balance being zirconium and any existing impurities of ordinary kind.
4. A method according to any of claims 1, 2 or 3, characterised in that the zirconium-based alloy used during the extrusion is .beta.-quenched.
5. A method according to any of claims 1, 2 or 3, characterised in that the extruded product is subjected to a final annealing at a temperature of 400-575°C after the last cold rolling.
6. A method according to claim 29 wherein the intermediate annealing is performed at a temperature of 550-600°C.
7. A method according to claim 6, wherein the zirconium-based alloy used during the extrusion is .beta.-quenched.
8. A method as claimed in claim 6, wherein the extruded product is subjected to a final annealing at a temperature of 400-675°C after the last cold rolling.
~ 7
~ 7
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| SE8104213A SE426890B (en) | 1981-07-07 | 1981-07-07 | SET TO MANUFACTURE Capsules of Zirconium-Based Alloy for Fuel Rods for Nuclear Reactors |
| SE8104213-7 | 1981-07-07 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CA1211344A true CA1211344A (en) | 1986-09-16 |
Family
ID=20344212
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA000406695A Expired CA1211344A (en) | 1981-07-07 | 1982-07-06 | Method of manufacturing cladding tubes of a zirconium- based alloy for fuel rods for nuclear reactors |
Country Status (9)
| Country | Link |
|---|---|
| JP (1) | JPS5825467A (en) |
| BE (1) | BE893787A (en) |
| CA (1) | CA1211344A (en) |
| DE (1) | DE3224686C2 (en) |
| ES (1) | ES8401665A1 (en) |
| FI (1) | FI72006C (en) |
| FR (1) | FR2509509B1 (en) |
| IT (1) | IT1191203B (en) |
| SE (1) | SE426890B (en) |
Families Citing this family (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4576654A (en) * | 1982-04-15 | 1986-03-18 | General Electric Company | Heat treated tube |
| JPS60165580A (en) * | 1984-02-08 | 1985-08-28 | 株式会社日立製作所 | Coated tube for reactor fuel and manufacture thereof |
| DE3429567A1 (en) * | 1984-08-10 | 1986-02-20 | Kraftwerk Union AG, 4330 Mülheim | METHOD FOR STABILIZING THE CORROSION RESISTANCE OF A PIPE PIPE MADE OF A ZIRCONIUM ALLOY FOR A CORE REACTOR FUEL |
| FR2575764B1 (en) * | 1985-01-10 | 1992-04-30 | Cezus Co Europ Zirconium | PROCESS FOR MANUFACTURING A STRIP OF ZIRCONIUM ALLOY ZIRCALOY 2 OR ZIRCALOY 4 RESTORED, AND STRIP OBTAINED |
| JP2600057B2 (en) * | 1985-12-09 | 1997-04-16 | 株式会社日立製作所 | Cladding tube, spacer, and channel box for highly corrosion resistant nuclear fuel, fuel assembly thereof, and method of manufacturing the same |
| JPH0625389B2 (en) * | 1985-12-09 | 1994-04-06 | 株式会社日立製作所 | Zirconium based alloy with high corrosion resistance and low hydrogen absorption and method for producing the same |
| JPS62195938U (en) * | 1986-05-31 | 1987-12-12 | ||
| US5437747A (en) * | 1993-04-23 | 1995-08-01 | General Electric Company | Method of fabricating zircalloy tubing having high resistance to crack propagation |
| SE514678C2 (en) * | 1998-11-12 | 2001-04-02 | Westinghouse Atom Ab | Process for producing a component exposed to elevated radiation in a corrosive environment |
| CN113667914B (en) * | 2021-08-09 | 2022-04-19 | 燕山大学 | A method for preparing high-strength pure zirconium by cold deformation |
Family Cites Families (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CA1014833A (en) * | 1974-07-12 | 1977-08-02 | Stuart R. Macewen | Zirconium base alloy and method of production |
| AU498717B2 (en) * | 1975-02-25 | 1979-03-22 | General Electric Company | Zirconium alloy heat treatment |
| FR2334763A1 (en) * | 1975-12-12 | 1977-07-08 | Ugine Aciers | PROCESS FOR IMPROVING THE HOT RESISTANCE OF ZIRCONIUM AND ITS ALLOYS |
| CA1139023A (en) * | 1979-06-04 | 1983-01-04 | John H. Davies | Thermal-mechanical treatment of composite nuclear fuel element cladding |
-
1981
- 1981-07-07 SE SE8104213A patent/SE426890B/en not_active IP Right Cessation
-
1982
- 1982-07-02 DE DE3224686A patent/DE3224686C2/en not_active Expired
- 1982-07-05 FR FR8211722A patent/FR2509509B1/en not_active Expired
- 1982-07-06 CA CA000406695A patent/CA1211344A/en not_active Expired
- 1982-07-06 FI FI822394A patent/FI72006C/en not_active IP Right Cessation
- 1982-07-06 JP JP57116328A patent/JPS5825467A/en active Granted
- 1982-07-06 IT IT67860/82A patent/IT1191203B/en active
- 1982-07-07 BE BE0/208547A patent/BE893787A/en not_active IP Right Cessation
- 1982-07-07 ES ES513793A patent/ES8401665A1/en not_active Expired
Also Published As
| Publication number | Publication date |
|---|---|
| IT8267860A0 (en) | 1982-07-06 |
| FR2509509A1 (en) | 1983-01-14 |
| FI72006B (en) | 1986-11-28 |
| DE3224686A1 (en) | 1983-01-27 |
| BE893787A (en) | 1982-11-03 |
| JPS5825467A (en) | 1983-02-15 |
| ES513793A0 (en) | 1983-12-16 |
| IT8267860A1 (en) | 1984-01-06 |
| FI822394L (en) | 1983-01-08 |
| JPS6151626B2 (en) | 1986-11-10 |
| SE8104213L (en) | 1983-01-08 |
| IT1191203B (en) | 1988-02-24 |
| DE3224686C2 (en) | 1987-02-19 |
| ES8401665A1 (en) | 1983-12-16 |
| SE426890B (en) | 1983-02-14 |
| FI72006C (en) | 1987-03-09 |
| FI822394A0 (en) | 1982-07-06 |
| FR2509509B1 (en) | 1985-07-12 |
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