JPH1036929A - Zirconium-base alloy plate reduced in irradiation growth, its production, and its use - Google Patents
Zirconium-base alloy plate reduced in irradiation growth, its production, and its useInfo
- Publication number
- JPH1036929A JPH1036929A JP9101282A JP10128297A JPH1036929A JP H1036929 A JPH1036929 A JP H1036929A JP 9101282 A JP9101282 A JP 9101282A JP 10128297 A JP10128297 A JP 10128297A JP H1036929 A JPH1036929 A JP H1036929A
- Authority
- JP
- Japan
- Prior art keywords
- zirconium
- fuel
- based alloy
- weight
- alloy
- 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.)
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Links
Classifications
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
- Y02E30/00—Energy generation of nuclear origin
- Y02E30/30—Nuclear fission reactors
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- Heat Treatment Of Articles (AREA)
- Monitoring And Testing Of Nuclear Reactors (AREA)
Abstract
Description
【0001】[0001]
【発明の属する技術分野】本発明は新規なジルコニウム
基合金板とその製造法及びそれを用いた燃料チャンネル
と燃料集合体に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a novel zirconium-based alloy plate, a method for producing the same, and a fuel channel and a fuel assembly using the same.
【0002】[0002]
【従来の技術】ジルコニウム合金は優れた耐食性と小さ
い中性子吸収断面積を有する材料であるため原子炉燃料
集合体部材に使用されている。前記用途にはジルカロイ
−2,ジルカロイ−4とよばれるZr−Sn−Fe−C
r−Ni合金が主に使用されている。これら合金の原子
炉内で長期間使用すると、図2に示すように(0001)
面が板厚方向に配向しているので、特定方向への伸び及
び曲がり変形が生じる。燃料チャンネルボックスに曲が
り変形が発生すると、制御棒が駆動するための間隙をふ
さぐため原子炉の運転に支障をきたす。また、曲がり変
形が生じると、燃料被覆管との間隔が変化し局部的に水
対ウランの比率が増減する為、核***反応度が変化す
る。この結果、異常発熱による燃料被覆管の腐食加速、
さらには燃料破損の原因にも成りうる。このような中性
子照射量の不均一に起因する燃料チャンネルボックスに
曲がり変形を防止する為、炉心における燃料集合体装荷
位置の入れ替えによる中性子照射量の均一化が検討され
ているが、曲がり変形を防止するは至らず、この曲がり
変形による制御棒駆動間隙の減少、核***反応度の変化
が燃料チャンネルボックスの寿命を制限する主因子とな
っている。2. Description of the Related Art Zirconium alloys have been used in reactor fuel assemblies because they are materials having excellent corrosion resistance and a small neutron absorption cross section. Zr-Sn-Fe-C called Zircaloy-2 or Zircaloy-4 is used for the above-mentioned applications.
An r-Ni alloy is mainly used. When these alloys are used for a long time in a nuclear reactor, (0001) as shown in FIG.
Since the surface is oriented in the thickness direction, elongation and bending deformation occur in a specific direction. If bending deformation occurs in the fuel channel box, the operation of the reactor is hindered because the gap for driving the control rod is closed. When bending deformation occurs, the interval between the fuel and the cladding tube changes, and the ratio of water to uranium locally increases or decreases, so that the fission reactivity changes. As a result, fuel cladding corrosion accelerated due to abnormal heat generation,
Furthermore, it may cause fuel damage. In order to prevent bending deformation of the fuel channel box due to such non-uniformity of neutron irradiation, it has been studied to make the neutron irradiation uniform by replacing the fuel assembly loading position in the reactor core. However, the reduction of the control rod driving gap and the change in fission reactivity due to the bending deformation are the main factors that limit the life of the fuel channel box.
【0003】燃料チャンネルボックスの腐食もその寿命
を制限する因子である。耐食性の改善方法としてZr合
金をα+β相温度範囲あるいはβ相温度範囲から急冷す
る熱処理が特許公報昭56−12310 号,昭60−44387 号に
開示されている。しかし、後述する理由により照射成長
に起因する曲がり変形を低減出来ない為、ジルコニウム
合金部材の照射成長抑制技術とはなり得ていない。[0003] Corrosion of the fuel channel box is also a factor that limits its life. As a method for improving the corrosion resistance, heat treatment for rapidly cooling the Zr alloy from the α + β phase temperature range or the β phase temperature range is disclosed in Japanese Patent Publication Nos. 56-12310 and 60-44387. However, since the bending deformation due to irradiation growth cannot be reduced for the reasons described below, it cannot be a technique for suppressing irradiation growth of a zirconium alloy member.
【0004】[0004]
【発明が解決しようとする課題】上記従来技術は、ジル
コニウム合金部材の結晶粒度,配向,機械特性等は熱処
理によって変化させず、耐食性のみを改善するものであ
る。その結果、結晶粒の粗大化が生じるβ相温度範囲
(≧980℃)よりもα+β相温度範囲(800〜98
0℃)への加熱・急冷が実施され、照射成長抑制に重要
な因子である結晶方位はこの熱処理では変化しない為、
ジルコニウム合金部材の照射成長抑制技術とはならなか
った。公開特許公報昭59−229475号にはFl値を0.1
5〜0.5に配向させる方法が開示されている。しか
し、この方法も後述する理由により照射成長抑制技術と
はならず、むしろ照射成長を促進する。In the above prior art, the grain size, orientation, mechanical properties, etc. of the zirconium alloy member are not changed by heat treatment, and only the corrosion resistance is improved. As a result, the α + β temperature range (800 to 98 ° C.) is more than the β phase temperature range (≧ 980 ° C.) in which the crystal grains are coarsened.
(0 ° C.), and the crystal orientation, which is an important factor in suppressing irradiation growth, is not changed by this heat treatment.
It did not become a technique for suppressing irradiation growth of zirconium alloy members. Published Patent Application No. 59-229475 discloses that the Fl value is 0.1.
A method for orienting to 5-0.5 is disclosed. However, this method is not an irradiation growth suppression technique for the reason described later, but rather promotes irradiation growth.
【0005】本発明は前述した照射成長に起因する伸
び,曲がり変形が発生しないジルコニウム合金部材を提
供することを目的とする。特に、照射成長しない長寿命
のジルコニウム基合金管状部材とそれを用いたチャンネ
ルボックスを提供することが本発明の主目的である。[0005] It is an object of the present invention to provide a zirconium alloy member which does not cause elongation and bending deformation due to the above-mentioned irradiation growth. In particular, it is a main object of the present invention to provide a long-life zirconium-based alloy tubular member that does not grow by irradiation and a channel box using the same.
【0006】[0006]
【課題を解決するための手段】本発明は、ジルコニウム
合金板材の六方晶Zr金属の〈0001〉結晶方位を図
1に示す様にほぼ完全にランダム化することにより上記
目的を達成するものである。The present invention achieves the above object by randomizing the <0001> crystal orientation of the hexagonal Zr metal of the zirconium alloy sheet material almost completely as shown in FIG. .
【0007】本発明は、Sn5重量%以下及び/又はN
b5重量%以下を含有し、90重量%以上のZrを有す
るジルコニウム基合金板において、該合金の六方晶Zr
の〈0001〉結晶方位の板表面に対する垂直方向への
配向率(Fr値)が0.20〜0.50 であることを特徴と
する低照射成長ジルコニウム基合金板にある。[0007] The present invention relates to a method for producing a steel sheet, comprising:
b in a zirconium-based alloy plate containing not more than 5% by weight and having not less than 90% by weight of Zr,
A low-irradiation-grown zirconium-based alloy sheet, characterized in that the <0001> crystal orientation has an orientation ratio (Fr value) in the direction perpendicular to the sheet surface of 0.20 to 0.50.
【0008】本発明は、Sn5重量%以下及び/又はN
b5重量%以下を含有し、90重量%以上のZrを有す
るジルコニウム基合金角形筒状部材において、該合金の
六方晶Zrの〈0001〉結晶方位の筒状部材表面に対
する垂直方向への配向率(Fr値),筒状部材の長手方
向への配向率(Ft)及び円周方向への配向率(Fl)
がいずれも0.20〜0.50であることを特徴とする低
照射成長ジルコニウム基合金管状部材にある。[0008] The present invention relates to a method for producing a steel sheet containing 5% by weight or less of Sn and / or N
b In a zirconium-based alloy rectangular tubular member containing 5 wt% or less and having Zr of 90 wt% or more, the orientation ratio of the <0001> crystal orientation of hexagonal Zr of the alloy in the direction perpendicular to the surface of the tubular member ( Fr value), the orientation ratio (Ft) of the cylindrical member in the longitudinal direction, and the orientation ratio (Fl) in the circumferential direction.
Are in the range of 0.20 to 0.50.
【0009】本発明は、Sn5重量%以下及び/又はN
b5重量%以下を含有し、90重量%以上のZrを有す
るジルコニウム基合金板において、該合金はα相を有
し、結晶粒径が50〜500μmであることを特徴とす
る低照射成長ジルコニウム基合金板にある。The present invention relates to a method for producing a steel sheet, comprising:
b. A low-irradiation-grown zirconium-based alloy plate containing 5% by weight or less and having a Zr of 90% by weight or more, wherein the alloy has an α phase and a crystal grain size of 50 to 500 μm. On the alloy plate.
【0010】本発明は、Sn5重量%以下及び/又はN
b5重量%以下を含有し、90重量%以上のZrを有す
るジルコニウム基合金板において、該合金はα相を有
し、該合金の六方晶Zrの〈0001〉結晶方位が実質
的にランダムに配向し、1022n/cm2 の中性子照射成
長によるひずみが3×10-4以下であることを特徴とす
る低照射成長ジルコニウム基合金板にある。[0010] The present invention relates to a method for producing a steel sheet, comprising:
b In a zirconium-based alloy plate containing 5% by weight or less and having Zr of 90% by weight or more, the alloy has an α phase, and the <0001> crystal orientation of hexagonal Zr of the alloy is substantially randomly oriented. And a low-irradiation-grown zirconium-based alloy plate, wherein the strain due to neutron irradiation growth of 10 22 n / cm 2 is 3 × 10 −4 or less.
【0011】本発明は、ジルコニウム基合金板をβ相単
相温度領域に加熱し、冷却するジルコニウム基合金板の
製造法において、該合金の六方晶Zrの〈0001〉結
晶方位の板表面に対する垂直方向への配向率(Fr値)
が0.26〜0.40となるように前記β相単相温度領域
にて加熱保持する工程を有することを特徴とする低照射
成長ジルコニウム基合金板の製造方法にある。According to the present invention, there is provided a method for producing a zirconium-based alloy plate in which a zirconium-based alloy plate is heated to a β-phase single-phase temperature region and cooled, wherein the <0001> crystal orientation of hexagonal Zr of the alloy is perpendicular to the plate surface. Orientation ratio (Fr value)
A low irradiation growth zirconium-based alloy plate, comprising a step of heating and maintaining the β-phase in the single-phase temperature range so that the value is 0.26 to 0.40.
【0012】本発明の低照射成長ジルコニウム基合金板
の製造法において、前記β相温度領域での加熱を次式に
よって求められるパラメータPの値が0.8 〜5になる
ように短時間保持後急冷する工程を有することを特徴と
する。In the method for producing a low-irradiation-grown zirconium-based alloy sheet of the present invention, the heating in the β-phase temperature range is maintained for a short time so that the value of a parameter P obtained by the following equation becomes 0.8 to 5. It has a step of quenching.
【0013】P=logt×log(T−980) (t:加熱時間(秒),T:加熱温度(℃)) 本発明は、ジルコニウム基合金角形筒状部材を局部的に
β相単相温度領域に誘導加熱によって相対的に移動させ
ながら連続的に加熱するとともに該加熱された部分を冷
媒によって強制的に冷却するジルコニウム基合金筒状部
材の製造法において、前記合金の六方晶Zrの〈000
1〉結晶方位の筒状部材表面に対する垂直方向への配向
率(Fr値)が0.20〜0.50となるように前記β相
単相温度領域にて加熱保持後急冷する工程を有すること
を特徴とする低照射成長ジルコニウム基合金筒状部材の
製造法にある。P = logt × log (T-980) (t: heating time (second), T: heating temperature (° C.)) The present invention provides a method of locally heating a zirconium-based alloy rectangular cylindrical member to a β-phase single-phase temperature. In a method for manufacturing a zirconium-based alloy tubular member in which a region is continuously heated while being relatively moved by induction heating and the heated portion is forcibly cooled by a refrigerant, a hexagonal Zr of the alloy is preferably <000.
1) A step of rapidly cooling after heating and holding in the β-phase single-phase temperature region so that the orientation ratio (Fr value) of the crystal orientation in the direction perpendicular to the surface of the cylindrical member is 0.20 to 0.50. A method for producing a low-irradiation-grown zirconium-based alloy cylindrical member characterized by the following characteristics.
【0014】本発明は、ジルコニウム基合金管状部材を
β相温度領域に局部的に誘導加熱によって相対的に移動
させながら連続的に加熱するとともに該加熱された部分
を冷媒によって強制的に冷却する際、前記管状部材内に
前記合金の熱膨脹係数が大きい金属部材からなるマンド
レルを挿入し、前記管状部材の少なくとも両端で管状部
材とマンドレルとを固着した状態で前記管状部材の外表
面より加熱する工程を有することが好ましい。The present invention relates to a method for continuously heating a zirconium-based alloy tubular member in a β-phase temperature region while locally moving it relatively by induction heating, and forcibly cooling the heated portion with a refrigerant. A step of inserting a mandrel made of a metal member having a large thermal expansion coefficient of the alloy into the tubular member, and heating from the outer surface of the tubular member in a state where the tubular member and the mandrel are fixed at at least both ends of the tubular member. It is preferred to have.
【0015】本発明は、ジルコニウム基合金部材製角形
筒状部材からなる燃料チャンネルボックスにおいて、前
記合金の六方晶Zrの〈0001〉結晶方位の筒状部材
表面に対する垂直方向への配向率(Fr値)が0.20
〜0.50であり、好ましくは前記管状部材全表面にオ
ートクレーブ処理による酸化皮膜が形成されているもの
が好ましい。According to the present invention, there is provided a fuel channel box comprising a rectangular cylindrical member made of a zirconium-based alloy member, wherein the hexagonal Zr of the alloy has a <0001> crystal orientation in a direction perpendicular to the surface of the cylindrical member (Fr value). ) Is 0.20
~ 0.50, preferably an oxide film formed on the entire surface of the tubular member by autoclave treatment.
【0016】本発明は、燃料ペレットを燃料被覆管内に
内蔵した燃料棒、該燃料棒を複数本収納するジルコニウ
ム基合金製燃料チャンネルボックス、該チャンネルボッ
クス内の前記燃料棒の間を仕切るスペーサ、前記チャン
ネルボックスの上部及び下部に設けられた上部格子板及
び下部格子板を備えた燃料集合体において、前記合金の
六方晶Zrの〈0001〉結晶方位の板表面に対する垂
直方向への配向率(Fr値)が0.20〜0.50である
ことを特徴とする燃料集合体にある。According to the present invention, there is provided a fuel rod containing fuel pellets in a fuel cladding tube, a fuel channel box made of a zirconium-based alloy for accommodating a plurality of the fuel rods, a spacer partitioning the fuel rods in the channel box, In a fuel assembly including an upper lattice plate and a lower lattice plate provided at the upper and lower portions of a channel box, the orientation ratio of the <0001> crystal orientation of the hexagonal Zr of the alloy in the direction perpendicular to the plate surface (Fr value) ) Is 0.20 to 0.50.
【0017】本発明は、複数本の原子燃料棒を配置する
ジルコニウム基合金からなるチャンネルボックスで、前
記合金は1022n/cm2 以上の中性子照射成長によるひ
ずみが3×10-4以下であり、少なくとも1回原子燃料
を取替えて使用することを特徴とする。According to the present invention, there is provided a channel box comprising a zirconium-based alloy in which a plurality of nuclear fuel rods are arranged, wherein the alloy has a strain of 3 × 10 −4 or less due to neutron irradiation growth of 10 22 n / cm 2 or more. , Characterized in that the nuclear fuel is replaced and used at least once.
【0018】本発明は、ジルコニウム基合金部材製筒状
部材からなる燃料チャンネルボックスで、前記合金は1
022n/cm2 以上の中性子照射成長によるひずみが3×
10-4以下であり、前記筒状部材全表面にオートクレーブ
処理による酸化皮膜が形成され、取出燃焼度32GWd
/t以上又は少なくとも1回原子燃料を交換して使用す
ることを特徴とする。The present invention relates to a fuel channel box comprising a cylindrical member made of a zirconium-based alloy member, wherein the alloy comprises
Strain due to neutron irradiation growth of 0 22 n / cm 2 or more is 3 ×
10 -4 or less, an oxide film is formed on the entire surface of the cylindrical member by an autoclave treatment, and the discharged burnup is 32 GWd.
It is characterized by exchanging the nuclear fuel at least / t or at least once.
【0019】本発明は、燃料ペレットを燃料被覆管内に
内蔵した燃料棒、該燃料棒を複数本収納するジルコニウ
ム基合金製燃料チャンネルボックス、該チャンネルボッ
クス内の前記燃料棒の間を仕切るスペーサ、前記チャン
ネルボックスの上部及び下部に設けられた上部格子板及
び下部格子板を備えた燃料集合体で、前記合金の六方晶
Zrの〈0001〉結晶方位の板表面に対する垂直方向
への配向率(Fr値)が0.20〜0.50あり、取出燃
焼度32GWd/t以上又は少なくとも1回原子燃料を
取替えて使用することを特徴とする。The present invention provides a fuel rod containing a fuel pellet in a fuel cladding tube, a fuel channel box made of a zirconium-based alloy containing a plurality of the fuel rods, a spacer for partitioning the fuel rods in the channel box, In a fuel assembly including an upper lattice plate and a lower lattice plate provided at an upper part and a lower part of a channel box, an orientation ratio (Fr value) of a hexagonal Zr of the alloy in a <0001> crystal orientation in a direction perpendicular to a plate surface is obtained. ) Is 0.20 to 0.50, and the burnout is 32 GWd / t or more or at least one time when the nuclear fuel is replaced and used.
【0020】本発明は炉心内にジルコニウム基合金の筒
状体よりなる複数の原子燃料チャンネルボックスを備
え、所定期間運転後に燃料を取換え、引き続いて所定期
間運転する原子炉の運転方法において、前記合金は10
22n/cm2 以上の中性子照射成長によるひずみが3×1
0-4以下であり、取出燃焼度32GWd/t以上の運転
又は前記後の運転時の前記チャンネルボックスの位置を
前の運転時の位置と同じに配置して少なくとも1回燃料
を取替えて運転することを特徴とする。The present invention relates to a method for operating a nuclear reactor, comprising a plurality of nuclear fuel channel boxes formed of a cylindrical body of a zirconium-based alloy in a reactor core, replacing fuel after a predetermined period of operation, and subsequently operating for a predetermined period. Alloy is 10
Strain due to neutron irradiation growth of 22 n / cm 2 or more is 3 × 1
0-4 or less, the position of the channel box at the time of operation with a discharge burnup of 32 GWd / t or more or the subsequent operation is the same as the position at the time of the previous operation, and the fuel is changed at least once to operate. It is characterized by the following.
【0021】前述のチャンネルボックスは少なくとも1
回燃料を取替えるだけでなく、取出燃焼度32GWd/
t以上又は中性子照射量で1022n/cm以上の中性子照
射を受ける期間変形が少なく使用することができる。The aforementioned channel box has at least one
In addition to changing fuel, the removal burn-up 32 GWd /
It can be used with little deformation during neutron irradiation of at least t or at least 10 22 n / cm in neutron irradiation amount.
【0022】特に、取出し燃焼度として38GWd/t
以上又は45GWd/t以上の高燃焼度側での使用が可
能になるとともに、より効果が顕著となる。In particular, the removal burnup is 38 GWd / t
It can be used on the high burn-up side of 45 GWd / t or more, and the effect becomes more remarkable.
【0023】本発明は、Sn5重量%以下及び/又はN
b5重量%以下を含有し、90重量%以上のZrを有す
る燃料チャンネルボックスにおいて、前記合金の六方晶
Zrの〈0001〉結晶方位の板表面に対する垂直方向
への配向率(Fr値)が0.20〜0.50 であることを特
徴とする。The present invention relates to a method for producing a steel sheet, comprising:
b In a fuel channel box containing 5% by weight or less and having Zr of 90% by weight or more, the orientation ratio (Fr value) of hexagonal Zr of the alloy in the <0001> crystal orientation in the direction perpendicular to the plate surface is 0.20 to 0.50.
【0024】本発明は、Sn5重量%以下及び/又はN
b5重量%以下を含有し、90重量%以上のZrを有す
るジルコニウム基合金板製角形筒状部材からなる燃料チ
ャンネルボックスにおいて、該合金の六方晶Zrの〈0
001〉結晶方位の筒状部材表面に対する垂直方向への
配向率(Fr値)が0.25〜0.50、筒状部材の長手
方向への配向率(Ft)が0.25〜0.36及び円筒方
向への配向率(Fl)が0.25〜0.36であることを
特徴とする。The present invention relates to a method for producing a steel sheet, comprising:
b In a fuel channel box comprising a rectangular cylindrical member made of a zirconium-based alloy plate containing 5% by weight or less and having 90% by weight or more of Zr, a value of <0 of hexagonal Zr of the alloy is used.
001> The orientation ratio (Fr value) of the crystal orientation in the direction perpendicular to the surface of the tubular member is 0.25 to 0.50, and the orientation ratio (Ft) in the longitudinal direction of the tubular member is 0.25 to 0.36. And the orientation ratio (Fl) in the cylindrical direction is 0.25 to 0.36.
【0025】本発明は、Sn5重量%以下及び/又はN
b5重量%以下を含有し、90重量%以上のZrを有す
るジルコニウム基合金板製角形筒状部材からなる燃料チ
ャンネルボックスにおいて、前記合金はその六方晶Zr
の〈0001〉結晶方位の筒状部材表面に対する垂直方
向への配向率(Fr値)が0.20〜0.50であり、そ
の結晶粒径が50〜500μmであることを特徴とす
る。According to the present invention, Sn is used in an amount of 5% by weight or less and / or N
b In a fuel channel box comprising a rectangular tubular member made of a zirconium-based alloy plate containing 5% by weight or less and having 90% by weight or more of Zr, the alloy has a hexagonal Zr
Is characterized in that the <0001> crystal orientation has an orientation ratio (Fr value) in the direction perpendicular to the surface of the cylindrical member of 0.20 to 0.50 and a crystal grain size of 50 to 500 μm.
【0026】本発明は、ジルコニウム基合金の角形筒状
部材からなる燃料チャンネルボックスにおいて、前記合
金はその六方晶Zrの〈0001〉結晶方位が実質的に
ランダムに配向し、1022n/cm2 の中性子照射成長に
よるひずみが3×10-4以下であることを特徴とする。According to the present invention, there is provided a fuel channel box comprising a rectangular cylindrical member made of a zirconium-based alloy, wherein the alloy has a <0001> crystal orientation of hexagonal Zr substantially randomly oriented, and 10 22 n / cm 2. Wherein the strain due to neutron irradiation growth is 3 × 10 −4 or less.
【0027】前述した変形は、図2に示す様に六方晶Z
r金属の〈0001〉結晶方位がジルコニウム合金表面
に垂直に配向するために起こる。六方晶Zr金属が中性
子照射を受けると、〈0001〉方向に結晶は収縮し
〈0001〉方向と直角な方向に膨脹する。より厳密に
述べると、中性子照射によって(0001)面に垂直な原
子面(転位)が導入され、上記結晶の収縮,膨脹が生じ
る。その結果、〈0001〉結晶方位が表面に垂直に配向し
た燃料チャンネルボックスでは長手方向及び幅方向に照
射成長する。炉心中央に近い程中性子照射量は多く、中
性子照射量が異なると照射成長量に差が生じ曲がり変形
が原因となる。照射成長の抑制には〈0001〉結晶方位の
ランダム化が有効である。照射成長は、体積変化を伴わ
ない変形である為、多結晶体の個々の結晶粒が特定方向
へ変形しても、その方向はランダムであるので全体的に
は変形しないのに等しい。The deformation described above is based on the hexagonal Z as shown in FIG.
This occurs because the <0001> crystal orientation of the r metal is oriented perpendicular to the zirconium alloy surface. When the hexagonal Zr metal receives neutron irradiation, the crystal contracts in the <0001> direction and expands in a direction perpendicular to the <0001> direction. Strictly speaking, neutron irradiation introduces an atomic plane (dislocation) perpendicular to the (0001) plane, causing the crystal to shrink and expand. As a result, in the fuel channel box in which the <0001> crystal orientation is oriented perpendicular to the surface, irradiation growth occurs in the longitudinal direction and the width direction. The closer to the center of the reactor core, the greater the neutron irradiation dose. If the neutron irradiation dose is different, the irradiation growth amount will differ, causing bending deformation. Randomization of <0001> crystal orientation is effective for suppressing irradiation growth. Irradiation growth is a deformation that does not involve a change in volume. Therefore, even if individual crystal grains of a polycrystal are deformed in a specific direction, the direction is random, and therefore, it is equivalent to no deformation as a whole.
【0028】結晶方位の配向の定量評価には、通常、反
射及び透過X線回折法の組合わせにより特定結晶面のX
線回折強度を測定し、測定されたX線回折強度から数1
によりF値を算出する方法が一般的である。In order to quantitatively evaluate the orientation of the crystal orientation, usually, the X-ray of a specific crystal plane is determined by a combination of reflection and transmission X-ray diffraction methods.
X-ray diffraction intensity was measured, and from the measured X-ray diffraction intensity,
Is generally used to calculate the F-number.
【0029】[0029]
【数1】 (Equation 1)
【0030】数1において、φは、特定方向(例えば、
板表面と垂直方向)と特定結晶方位(例えば、〈000
2〉結晶方位)とのなす角度であり、V(φ)は、φ方向
に配向した結晶の体積率である。r方向,t方向,l方
向を、それぞれ互いに直角な板(管)表面の法線方向(F
r),板(管)の長手方向(Ft),板幅(管円周)方向
(Fl)と定義すると、次式 Fr+Ft+Fl=1.0 の関係にあり、完全に結晶方位がランダム化すると、 Fr=Ft=Fl=1/3 となる。In equation (1), φ represents a specific direction (for example,
Specific crystal orientation (for example, <000
2> crystal orientation), and V (φ) is the volume fraction of the crystal oriented in the φ direction. The r-direction, t-direction, and l-direction are defined as normal directions (F
r), the longitudinal direction (Ft) of the plate (tube), and the plate width (pipe circumference) direction (Fl), there is a relationship of Fr + Ft + Fl = 1.0, and if the crystal orientation is completely randomized, Fr = Ft = Fl = 1/3.
【0031】Fr,Ft及びFlのいずれも0.20〜
0.50となるようにすること、Fr0.25〜0.5
0,Fl0.25〜0.36,Ft0.25〜0.36とす
ることが好ましく、特にいずれも0.31〜0.35が最
も好ましい。Each of Fr, Ft and Fl is 0.20 to
0.50, Fr 0.25 to 0.5
It is preferable to set it to 0.2, Fl 0.25 to 0.36, Ft 0.25 to 0.36, and particularly to 0.31 to 0.35.
【0032】通常の冷間加工及び焼鈍のくり返しによる
製造プロセスに従って製造された板及び管の(000
2)結晶面(:0001)面と等価)のFr値は0.6
前後となり、〈0001〉結晶方位は、主に板(管)の表
面法線方向に配向している。このように、表面法線方向
に〈0001〉結晶方位が配向した状態を集合組織と言
う。図3は、中性子照射量と照射伸びとの関係につい
て、Fr値をパラメーターとして示す。Fr値が0.5
0以下好ましくは0.45以下になると照射伸びは著し
く減少し、Fr値を0.333〜0.350とすることに
より中性子照射量≧1022(n/cm2)高照射域において
も伸びが実質的に0(ゼロ)となることが分かる。(000) of plates and tubes manufactured according to the normal cold working and repeated annealing process.
2) The Fr value of the crystal plane (equivalent to the: 0001) plane is 0.6.
Before and after, the <0001> crystal orientation is mainly oriented in the surface normal direction of the plate (tube). Such a state in which the <0001> crystal orientation is oriented in the surface normal direction is called texture. FIG. 3 shows the relationship between the neutron irradiation amount and the irradiation elongation using the Fr value as a parameter. Fr value is 0.5
When it is 0 or less, preferably 0.45 or less, the irradiation elongation is remarkably reduced, and by setting the Fr value to 0.333 to 0.350, the elongation can be increased even in a high irradiation range of neutron irradiation ≧ 10 22 (n / cm 2 ). It turns out that it becomes substantially 0 (zero).
【0033】Fr値≦0.50 となる集合組織を得る一
手段として、ジルコニウム合金部材をβ相温度範囲(ジ
ルカロイ合金では980℃を越える温度)まで加熱し、
かつβZr結晶粒を十分成長させた後、冷却特に水噴霧
によって急冷する方法である。この処理を行うことによ
り六方晶αZr結晶は立方晶βZr結晶へと変態し、冷
却過程で再び六方晶αZr結晶へと再変態する。この熱
処理において、Fr値0.333〜0.350となる集合
組織を得るにはβZr結晶粒が少なくとも100μm以上
に成長するのが良く、Fr値≦0.50 となる集合組織
を得るにはβZr結晶粒が少なくとも50μm以上500
μm以下、好ましくは150μm以上300μm以下で
ある。β相温度での加熱時間はβ相温度範囲の高温域ほ
ど(好ましくは1100〜1350℃より好ましくは1
100〜1200℃)短時間で加熱することができる。
最高加熱温度での保持時間はほんの短い時間で行うこと
ができ、例えば1.5〜600秒、好ましくは1.5秒〜
100秒、より好ましくは5〜60秒である。特に、図
8で●印の範囲で行うのが好ましい。As one means for obtaining a texture that satisfies the Fr value ≦ 0.50, the zirconium alloy member is heated to a β-phase temperature range (a temperature exceeding 980 ° C. for a zircaloy alloy),
In this method, the βZr crystal grains are sufficiently grown and then rapidly cooled by cooling, particularly by water spray. By performing this treatment, the hexagonal αZr crystal is transformed into a cubic βZr crystal, and is transformed again into a hexagonal αZr crystal during the cooling process. In this heat treatment, βZr crystal grains should grow to at least 100 μm or more in order to obtain a texture having a Fr value of 0.333 to 0.350, and βZr should be obtained in order to obtain a texture having a Fr value ≦ 0.50. The crystal grain is at least 50 μm or more and 500
μm or less, preferably 150 μm or more and 300 μm or less. The heating time at the β-phase temperature is higher in the β-phase temperature range (preferably 1100 to 1350 ° C., more preferably 1 to 1350 ° C.).
(100-1200 ° C) can be heated in a short time.
The holding time at the maximum heating temperature can be performed in a very short time, for example, 1.5 to 600 seconds, preferably 1.5 seconds to
It is 100 seconds, more preferably 5 to 60 seconds. In particular, it is preferable to perform the processing in the range indicated by the mark in FIG.
【0034】α+β相温度範囲の加熱では変態しないα
Zr結晶が残存するため、好ましい集合組織は得られな
い。また、β相温度範囲に加熱してもその保持時間が短
く、かつ加熱温度が低いと好ましい集合組織は得られな
い。その理由は、αZrからβZrへの変態(加熱過
程)及びβZrからαZrへの変態(冷却過程)におい
て、αZrの(0001)結晶面とβ−Zrの(11
0)結晶面とが平行になる結晶方位関係を保持しながら
変態が進行するため、加熱・冷却終了後になんら結晶方
位の変化が生じないからである。ランダムな結晶方位の
配向の集合組織を得るには、種々の結晶方位を有するβ
Zr結晶粒が成長することが必要であり、そのために
は、βZr結晶粒が少なくとも50μm以上に成長する
に十分な温度あるいは保持時間(P値で0.8以上)を
必要とする。The α is not transformed by heating in the α + β phase temperature range.
Since Zr crystals remain, a favorable texture cannot be obtained. In addition, even if heating is performed in the β-phase temperature range, if the holding time is short and the heating temperature is low, a favorable texture cannot be obtained. The reason is that in the transformation from αZr to βZr (heating process) and the transformation from βZr to αZr (cooling process), the (0001) crystal plane of αZr and (11
0) The transformation proceeds while maintaining the crystal orientation relationship in which the crystal plane is parallel to the crystal plane, so that no change in the crystal orientation occurs after the completion of heating and cooling. In order to obtain a texture having a random crystal orientation, β having various crystal orientations should be used.
It is necessary that Zr crystal grains grow, and for that, a temperature or holding time (P value of 0.8 or more) sufficient for βZr crystal grains to grow to at least 50 μm or more is required.
【0035】上述の如く、熱処理によってFr値は変わ
るが、その温度と保持時間で重要な要因である。従っ
て、β相温度領域でFr値が0.50 以下になるように
するには前述の式によって求められるパラメータPが
1.5 以上(βZr結晶粒60μm以上)となるように
することが必要である。As described above, the Fr value changes depending on the heat treatment, but it is an important factor depending on the temperature and the holding time. Therefore, in order for the Fr value to be 0.50 or less in the β-phase temperature region, it is necessary to set the parameter P obtained by the above equation to be 1.5 or more (βZr crystal grains 60 μm or more). is there.
【0036】更に、パラメータPは2.5 〜5(βZr
結晶粒70〜500μm)が好ましく、特に3.2〜5
(βZr結晶粒100〜500μm)が好ましい。Further, the parameter P is 2.5 to 5 (βZr
Crystal grains 70 to 500 μm) are preferred, and especially 3.2 to 5 μm.
(ΒZr crystal grains 100 to 500 μm) is preferred.
【0037】ジルコニウム基合金として、Sn5重量%
以下及び又はNb5重量%以下、及び残部90重量%以
上(好ましくは95〜98.5 重量%)のZrを有する
ジルコニウム基合金からなる。Sn及びNbはZrの強
度を高めるに必要なもので、前者が3%,後者が5%以
下必要である。下限として、各々0.1 %が好ましい。
ジルカロイ系合金として、Snは1〜2%が好ましく、
特に1.2〜1.7%が好ましい。この合金にはFe0.
5%以下,Cr0.5%以下、又はこのCrとNi0.2
%以下、又はこれらのFeとNiを含むことができ、特
にFe0.1〜0.38%,Cr0.05〜0.15%,N
i0.03〜1.25% を含むもの、Fe0.22〜0.
38%,Cr0.05〜0.15%及びNi0.09〜0.
15%を含むもの、後者のFe及びNiは単独でもよい
が複合が好ましく、(Fe/Ni)比は1.3〜10が
好ましい。As a zirconium-based alloy, Sn 5% by weight
And / or Nb of 5% by weight or less, and a balance of 90% by weight or more (preferably 95 to 98.5% by weight) of a zirconium-based alloy having Zr. Sn and Nb are necessary to increase the strength of Zr, and the former needs 3% and the latter needs 5% or less. The lower limits are each preferably 0.1%.
As a zircaloy-based alloy, Sn is preferably 1 to 2%,
In particular, it is preferably from 1.2 to 1.7%. This alloy has Fe0.
5% or less, Cr 0.5% or less, or this Cr and Ni 0.2
% Or less, or Fe and Ni thereof, especially Fe 0.1 to 0.38%, Cr 0.05 to 0.15%, N
i containing 0.03 to 1.25%, Fe 0.22 to 0.25%
38%, Cr 0.05-0.15% and Ni 0.09-0.1.
The one containing 15%, the latter Fe and Ni may be used alone, but a composite is preferable, and the (Fe / Ni) ratio is preferably 1.3 to 10.
【0038】Nbを含む合金として、Zr−0.5〜2
%Nb,Zr−2〜5%Sn−0.5〜1.5%Nb−
0.5〜1.5%Mo,Zr−0.5〜0.15%Sn−
0.5〜1.5%Nb−0.1〜1.0%Fe,Zr−0.
5〜5.0%Nb−0〜3.0%Sn−2%以下のFe,
Ni,Cr,Ta,Pd,Mo,Wの1種又は2種以上
含む合金が用いられる。As an alloy containing Nb, Zr-0.5-2
% Nb, Zr-2 to 5% Sn-0.5 to 1.5% Nb-
0.5-1.5% Mo, Zr-0.5-0.15% Sn-
0.5 to 1.5% Nb-0.1 to 1.0% Fe, Zr-0.5.
Fe of 5 to 5.0% Nb-0 to 3.0% Sn-2% or less,
An alloy containing one or more of Ni, Cr, Ta, Pd, Mo, and W is used.
【0039】本発明の製造法として、β相温度領域での
加熱は板材を移動させながら誘導コイルによって連続的
に所望の保持時間加熱すると同時に加熱後に強制的に冷
却するもので、このβ相への加熱によって〈0001〉
方位がランダムになるとともに、高温高圧純水に対して
耐食性の高いものが得られる。冷却は噴水によって行う
のが好ましく、100℃/秒以上特に、150℃/秒以
上の冷却速度とするのがよい。加熱手段として他に赤外
線,電気炉が用いられる。According to the production method of the present invention, heating in the β-phase temperature range involves heating the sheet material continuously for a desired holding time by an induction coil while moving the sheet material and simultaneously forcibly cooling after the heating. <0001>
The orientation becomes random and a material having high corrosion resistance to high-temperature and high-pressure pure water is obtained. The cooling is preferably performed by a fountain, and is preferably performed at a cooling rate of 100 ° C./sec or more, particularly 150 ° C./sec or more. Infrared and electric furnaces are also used as heating means.
【0040】β相温度領域での加熱に際してZr基合金
より熱膨脹係数の大きい部材によって固定し拘束して行
うのがよく、特に管状部材の場合にはその内部に部材内
面に全面が接触しないよう熱の影響を少なくして部分的
に接するようにした金属部材を挿入するとともに両端を
互いに固定して加熱,冷却に際して管状部材が変形しな
いようにして加熱及び冷却を行うのが好ましい。このよ
うな拘束部材を設けることによって加熱及び冷却が容易
に行うことができる。拘束部材としてSUS304,316,
347等のZr基合金より熱膨脹係数の大きいオーステ
ナイト系ステンレス鋼が好ましい。When heating in the β-phase temperature region, it is preferable to fix and restrain the member by using a member having a higher thermal expansion coefficient than that of the Zr-based alloy. Particularly, in the case of a tubular member, heat is applied so that the entire surface does not contact the inner surface of the member. It is preferable to insert a metal member that is partially in contact with each other and to fix both ends to each other to perform heating and cooling so that the tubular member is not deformed during heating and cooling. By providing such a restraining member, heating and cooling can be easily performed. SUS304,316, as a restraining member
Austenitic stainless steel having a larger coefficient of thermal expansion than a Zr-based alloy such as 347 is preferable.
【0041】β領域での加熱処理は板材で行うか管状部
材で行うかのいずれでもよく、板材で行う方法はβ領域
で熱処理後に管状に成形して溶接によって接合される。The heat treatment in the β region may be performed with a plate or a tubular member. The method of performing the heat treatment with the plate is performed by heat treatment in the β region, then forming into a tube and joining by welding.
【0042】β相熱処理後、次いで全体を均一に加熱す
る焼鈍が行われる。焼鈍は500〜650℃(好ましく
は550〜640℃)で行われる。この焼鈍に際しても
前述の拘束部材によって拘束して行うのが好ましく、そ
れによって管状部材の整形を行うことができる。これら
の熱処理は非酸化性範囲気中で行われ、特にAr中で行
うのが好ましい。After the β-phase heat treatment, annealing is performed to uniformly heat the whole. Annealing is performed at 500 to 650 ° C (preferably 550 to 640 ° C). It is preferable that the annealing is also performed by restraining by the above-described restraining member, so that the tubular member can be shaped. These heat treatments are performed in a non-oxidizing range atmosphere, particularly preferably in Ar.
【0043】最終熱処理後は、サンドブラスト及び酸洗
によって表面の酸化皮膜が除去される。酸化皮膜が除去
された後、オートクレーブによって表面が酸化処理さ
れ、表面に安定な酸化皮膜が形成され、最終製品とされ
る。また、前述の両端部で固定するためのネジ穴等の端
部は除去されて使用される。After the final heat treatment, the oxide film on the surface is removed by sandblasting and pickling. After the oxide film is removed, the surface is oxidized by an autoclave, and a stable oxide film is formed on the surface to obtain a final product. In addition, the ends such as the screw holes for fixing at the both ends described above are used after being removed.
【0044】本発明のチャンネルボックスは2個のコの
字型部材を突合わせしプラズマ溶接されて角筒とした
後、この溶接部を平坦化して使用される。この角筒の熱
処理にはX字型の拘束部材を挿入して行うことが好まし
い。本発明の熱処理は板材の状態,コの字の状態又は溶
接後の角筒の状態のいずれでもよい。板材で熱処理した
ものはコの字に曲げ加工を施し、溶接によって角筒にし
て用いられる。In the channel box of the present invention, two U-shaped members are butted and plasma-welded to form a square tube, and this weld is flattened before use. It is preferable that the heat treatment of the rectangular tube is performed by inserting an X-shaped restraining member. The heat treatment of the present invention may be in any state of a plate material, a U-shape, or a rectangular tube after welding. The heat-treated plate is bent into a U-shape and welded into a rectangular tube.
【0045】[0045]
(実施例1)ジルコニウム合成板材として、表1に示す
合金組成を有する3種類のジルカロイを使用し、表2に
示す熱処理を施した。(Example 1) Three kinds of zircaloys having alloy compositions shown in Table 1 were used as zirconium composite sheet materials, and heat treatments shown in Table 2 were performed.
【0046】[0046]
【表1】 [Table 1]
【0047】[0047]
【表2】 [Table 2]
【0048】いずれの合金も厚さ2mmの板材であり、受
け入れ前に冷間圧延と650℃,2時間の焼鈍とを繰り
返し施されている。表2に示した熱処理No.2〜4は、
幅:40mm,長さ:40mmの試験片を受け入れ材から切
り出し、電気炉で加熱し、水中で冷却することにより行
ったものである。パラメータPは前述の式によって求め
たものである。No.1及び2は比較材、No.3〜6は本
発明材である。Each of the alloys is a plate having a thickness of 2 mm, and has been repeatedly subjected to cold rolling and annealing at 650 ° C. for 2 hours before receiving. Heat treatment Nos. 2 to 4 shown in Table 2
A test piece having a width of 40 mm and a length of 40 mm was cut out of a receiving material, heated in an electric furnace, and cooled in water. The parameter P is obtained by the above equation. Nos. 1 and 2 are comparative materials, and Nos. 3 to 6 are materials of the present invention.
【0049】表3はNo.1〜6熱処理材の(0002)
面(:(0001)面と平行)及び(1010)面(:
(0001)面と垂直)のF値測定結果を示す。F値測
定方法は前述した反射及び透過X線回折法の組合わせに
よって測定される。Frは管状部材において表面に対す
る垂直方向への配向率、Ftは長手方向への配向率、F
lは円周方向への配向率である。Table 3 shows (0002) of No. 1 to 6 heat-treated materials.
Plane (: parallel to the (0001) plane) and (1010) plane (:
The F-number measurement result of (perpendicular to (0001) plane) is shown. The F value is measured by a combination of the reflection and transmission X-ray diffraction methods described above. Fr is the orientation ratio in the direction perpendicular to the surface of the tubular member, Ft is the orientation ratio in the longitudinal direction, F
l is the orientation ratio in the circumferential direction.
【0050】[0050]
【表3】 [Table 3]
【0051】通常の冷間圧延と焼鈍とを繰り返して製造
した板材(熱処理No.1)では、(0002)面のFr
値は約0.7と高く、(1010)面のFr値(約0.1
5)はFl,Ft値に比べて低いことから、(000
2)面がほぼ板表面と平行に配向していることが表3の
結果より分かる。α+β相温度範囲への加熱・冷却板材
(熱処理No.2)のF値は受け入れ材(熱処理No.1)
とほぼ等しいことから、α+β相温度範囲への加熱・冷
却では集合組織は変化しないことが分かる。β相温度範
囲(1000℃)に1分間及び5秒保持後冷却した場合
(熱処理No.3,6)は受け入れ材に比べて、(000
2)面のFr値の減少、Fl,Ft値の増加及び(10
10)面のFr値の増加、Fl,Ft値の減少が認めら
れ、結晶方位がランダム化する。しかし、中性子照射量
≧1022(n/cm2)の高照射域においても使用可能とな
る為の目標値であるFr値≦0.35 を満足しない。1
000℃で10分間保持した場合(熱処理No.4)及び
1200℃まで加熱温度を高めた場合(熱処理No.5),
(0002),(1010)両面のいずれのF値も約0.33と
なり、結晶方位はほぼ完全にランダム化することが分か
る。前述したように、No.4,5熱処理材は高照射域
で、かつ部材内に中性子照射量の不均一があっても、曲
がり変形,伸び変形が生じない。In a sheet material (heat treatment No. 1) manufactured by repeating ordinary cold rolling and annealing, the (0002) plane Fr
The value is as high as about 0.7, and the Fr value of the (1010) plane (about 0.1
5) is lower than the Fl and Ft values,
2) It can be seen from the results in Table 3 that the plane is oriented substantially parallel to the plate surface. The F value of the heating / cooling plate material (heat treatment No. 2) within the α + β phase temperature range is the receiving material (heat treatment No. 1)
From the above, it is understood that the texture does not change by heating and cooling to the α + β phase temperature range. When cooled after holding for 1 minute and 5 seconds in the β-phase temperature range (1000 ° C.) (heat treatment No. 3, 6), (000
2) Decrease of Fr value of surface, increase of Fl and Ft values, and (10
10) An increase in the Fr value of the plane and a decrease in the Fl and Ft values are recognized, and the crystal orientation is randomized. However, it does not satisfy Fr value ≦ 0.35 which is a target value for being usable even in a high irradiation range of neutron irradiation amount ≧ 10 22 (n / cm 2 ). 1
When the temperature is kept at 000 ° C. for 10 minutes (heat treatment No. 4) and when the heating temperature is increased to 1200 ° C. (heat treatment No. 5),
The F value of both the (0002) and (1010) surfaces is about 0.33, indicating that the crystal orientation is almost completely randomized. As described above, the No. 4 and No. 5 heat-treated materials do not bend or elongate even in a high irradiation area and even when the neutron irradiation amount is uneven in the member.
【0052】図3は高速中性子照射量と照射成長ひずみ
との関係を示す線図である。図に示す如く、Fr値が
0.4 を越えると中性子照射量の増加とともに急激にひ
ずみが増加するが、0.4 以下では照射を受けてもひず
みは飽和し、増加しないことが分る。特に、Fr=0.
35 のものは<0001>結晶方位が実質的にランダ
ムに配向しているので、法線方向,長手方向及び板厚方
向におけるひずみが各結晶間で互いに相殺されるため
0.5×10-4以下と全く生じない。Fr=0.4のもの
は照射量3×1022n/cm2 まではひずみ量は小さい
が、それ以上の中性子照射量では徐々にひずみが多くな
る。しかし、Fr=0.35 では中性子照射量が増加し
てもひずみの増加は生じない。FIG. 3 is a diagram showing the relationship between the fast neutron irradiation dose and the irradiation growth strain. As shown in the figure, when the Fr value exceeds 0.4, the strain increases rapidly with an increase in the neutron irradiation dose, but when the Fr value is less than 0.4, the strain saturates even after irradiation, and does not increase. In particular, Fr = 0.
In the case of No. 35, since the <0001> crystal orientation is substantially randomly oriented, the strain in the normal direction, the longitudinal direction, and the thickness direction is canceled out among the respective crystals, so that 0.5 × 10 -4. The following does not occur at all. In the case of Fr = 0.4, the amount of strain is small up to the irradiation dose of 3 × 10 22 n / cm 2 , but the strain gradually increases with the neutron irradiation dose higher than that. However, when Fr = 0.35, the strain does not increase even if the neutron irradiation dose increases.
【0053】図4はFr値と、高速中性子3×1022n
/cm2 の照射による照射成長ひずみとの関係を示す線図
である。Fr値の増加とともにひずみが急激に増加す
る。特に、Fr=0.35 の照射成長のひずみは約0.
2×10-4で、Fr=0.4の約1.5×10-4 の約7
分の1と著しく少ない。また、Fr=0.4はFr=0.
5の約3分の1と著しく少ない。しかし、Fr=0.5
はFr=0.6の約半分、Fr=0.6はFr=0.7の
約半分であり、Frが0.4 を越えると大きな効果は得
られない。FIG. 4 shows the Fr value and fast neutrons 3 × 10 22 n
FIG. 2 is a diagram showing a relationship between irradiation and irradiation growth strain caused by irradiation at / cm 2 . The strain increases sharply as the Fr value increases. In particular, the irradiation growth strain at Fr = 0.35 is about 0.3.
2 × 10 -4 , about 1.5 × 10 -4 of Fr = 0.4 about 7
Significantly less than 1 /. Also, Fr = 0.4 is equivalent to Fr = 0.
It is remarkably small, about 1/3 of 5. However, Fr = 0.5
Is about half of Fr = 0.6, and Fr = 0.6 is about half of Fr = 0.7. If Fr exceeds 0.4, no great effect can be obtained.
【0054】No.1,3,4の各熱処理材の金属組織で
観察される丸みを帯びた結晶粒はαZrでありβZr結
晶粒は存在しなかった。図4(b)及び(c)において
観察される多角形状の結晶粒がβ相温度範囲加熱保持中
に形成されたβZr結晶粒であり、1000℃保持時間
が1分から10分と長くなるに従って、βZr結晶粒径
が大きく成長することが分かる。βZr結晶粒径内に見
られる層状あるいは針状の組織は、冷却過程でβZrが
再びαZrに変態する際に形成されたものであり、βZ
r結晶粒界ではない。The rounded crystal grains observed in the metal structures of the heat-treated materials of Nos. 1, 3, and 4 were αZr, and no βZr crystal grains were present. The polygonal crystal grains observed in FIGS. 4B and 4C are βZr crystal grains formed during heating and holding in the β phase temperature range, and as the holding time at 1000 ° C. increases from 1 minute to 10 minutes, It can be seen that the βZr crystal grain size grows large. The layered or acicular structure found in the βZr crystal grain size is formed when βZr is transformed again into αZr during the cooling process.
Not r grain boundaries.
【0055】図5は、βZr結晶粒径と(0002)面
のFr値との関係を示す。結晶粒径200μm以上にβ
Zr結晶粒が成長することによって、Fr値≦0.35
の集合組織が形成されることが分かる。FIG. 5 shows the relationship between the βZr crystal grain size and the Fr value of the (0002) plane. Β with a crystal grain size of 200 μm or more
By growing the Zr crystal grains, the Fr value ≦ 0.35
It can be seen that the texture of is formed.
【0056】結晶粒を成長させることによって(000
2)面の結晶方位をランダム化することができるが、そ
の方位のランダム化の度合としてFr値0.40 で約7
5%であり、そのときの粒径は約100μmである。1
50μm以上の大きさの結晶粒径とすることにより約8
0%以上にランダム化され、Fr値で0.385 とな
る。更にFr値0.35 でのランダム率は約90%以上
となり、そのときの結晶粒径は約250μm以上とな
る。By growing the grains (000
2) Although the crystal orientation of the plane can be randomized, the degree of randomization of the orientation is about 7 at a Fr value of 0.40.
5%, at which time the particle size is about 100 μm. 1
With a crystal grain size of 50 μm or more, about 8
It is randomized to 0% or more, and the Fr value becomes 0.385. Further, the random ratio at an Fr value of 0.35 is about 90% or more, and the crystal grain size at that time is about 250 μm or more.
【0057】図6はβZr結晶粒径と照射成長ひずみと
の関係を示す線図である。図より、粒径90μm以上で
ひずみ量が約1.5×10-4 と著しく低くなるが、更
に、150μm以上ではひずみは0.5×10-4 以下の
非常に小さなものとなる。特に、200μm以上では
0.3×10-4 程度となる。FIG. 6 is a graph showing the relationship between the βZr crystal grain size and the irradiation growth strain. As shown in the figure, when the particle size is 90 μm or more, the strain amount is remarkably low at about 1.5 × 10 −4 , but when the particle size is 150 μm or more, the strain becomes extremely small, 0.5 × 10 −4 or less. In particular, when the thickness is 200 μm or more, it is about 0.3 × 10 −4 .
【0058】図7はパラメータP=logt×log
(T−980)と照射成長ひずみとの関係を示す線図で
ある。図に示すように照射成長ひずみは熱処理における
温度と保持時間との関係によって決まるパラメータPに
よって大きく左右される。パラメータPはZrの〈00
01〉結晶方位の配向率を決める重要な因子となる。1
000℃での熱処理ではPが0.5 以上で照射成長ひず
みが急激に小さくなり、更に0.5〜3.5までは徐々に
小さくなり、3.5 以上ではほぼ一定となり零に近い。
Pが3.5 未満では照射成長が起こるが、それ以上では
ほとんど起こらない。FIG. 7 shows a parameter P = logt × log
It is a diagram which shows the relationship between (T-980) and irradiation growth strain. As shown in the figure, the irradiation growth strain is greatly affected by a parameter P determined by the relationship between the temperature and the holding time in the heat treatment. Parameter P is <00 of Zr
01> It is an important factor that determines the orientation ratio of the crystal orientation. 1
In the heat treatment at 000 ° C., the irradiation growth strain sharply decreases when P is 0.5 or more, further gradually decreases from 0.5 to 3.5, becomes almost constant at 3.5 or more, and approaches zero.
Irradiation growth occurs when P is less than 3.5, but hardly occurs above P.
【0059】特に、1.5以上で効果が大きく、3.2〜
5が好ましい。In particular, the effect is large at 1.5 or more and 3.2 to 3.2.
5 is preferred.
【0060】図8は、各温度と保持時間における表1及
び表4に示す合金の(0002)面のFl値の関係を示
す線図である。図に示すように980℃未満ではFl値
が0.20 以下となり〈0002〉方向の結晶方位がラ
ンダムなものが得られにくい。しかし、1000℃で1
0.5 秒以上加熱又は1240℃以上で2秒以上でこれ
らの点を結ぶ線上以上で加熱すればFl値として0.2
5 を越えるものが得られ、よりランダム度の高いもの
が得られる。また、980℃以上で6秒以上及び124
0℃以上で6秒以上で、これらの点を結ぶ線上以上で加
熱すればFl値が0.20より大きく0.25以下のもの
が得られる。この線上より低いものはFl値が0.20
以下となりランダム度が低く伸び量に対する効果が小さ
い。FIG. 8 is a graph showing the relationship between the Fl value of the (0002) plane of the alloys shown in Tables 1 and 4 at each temperature and holding time. As shown in the drawing, when the temperature is lower than 980 ° C., the Fl value becomes 0.20 or less, and it is difficult to obtain a crystal having a random <0002> crystal orientation. However, at 1000 ° C.
Heating for 0.5 seconds or more or heating at 1240 ° C. or more for 2 seconds or more and above the line connecting these points will give an Fl value of 0.2.
More than 5 are obtained, and those with a higher degree of randomness are obtained. At 980 ° C. or more, 6 seconds or more and 124
By heating at 0 ° C. or more for 6 seconds or more and above the line connecting these points, an Fl value greater than 0.20 and 0.25 or less can be obtained. Those lower than this line have an Fl value of 0.20.
Below, the degree of randomness is low and the effect on the amount of elongation is small.
【0061】[0061]
【表4】 [Table 4]
【0062】(実施例2)図9は、本発明に基づくチャ
ンネル・ボックス製作の一実施例を示す。実施例1で述
べたジルカロイ−C板材をコの字型に冷間曲げ加工し、
長さ4mの2つのコの字型部材とし、これらをプラズマ
溶接し、角筒1とした。溶接部の凹凸は平坦に仕上げら
れる。この角筒1の内部にSUS304ステンレス鋼製マンド
レル2を挿入し、端部をネジ3で固定し、高周波誘導加
熱によるβ相温度範囲への加熱及び高周波誘導加熱コイ
ル4の直下に設けたノズル6から吹き付ける冷却水で急
冷した。冷却水は温水も使用される。マンドレル2は被
加熱材に対する熱影響を少なくするように接触面積を小
さくするようにしている。角筒1は一定の速度で下から
上に移動させることによりその上方から下方へコイル内
を通過することにより、全体の熱処理が完了する。加熱
温度は1300℃,1200℃で保持時間は20秒及び
1100℃で保持時間10秒となるように角筒1の送り
速度及び高周波電源5の出力を調整した。熱処理完了
後、幅40mm,長さ40mmの試験片を切り出しX線回折
法によりF値を測定した。表5は、その測定結果を示
す。パラメータPは1300℃が3.26 、1200℃
が3.05及び1100℃が2.07である。(Embodiment 2) FIG. 9 shows an embodiment of manufacturing a channel box according to the present invention. The Zircaloy-C plate described in Example 1 was cold-bent into a U-shape,
Two U-shaped members having a length of 4 m were formed, and these were plasma-welded to form a square tube 1. The unevenness of the weld is finished flat. A mandrel 2 made of SUS304 stainless steel is inserted into the inside of this square tube 1, the end is fixed with a screw 3, heating to a β-phase temperature range by high-frequency induction heating, and a nozzle 6 provided immediately below a high-frequency induction heating coil 4. And quenched with cooling water. Hot water is also used as cooling water. The contact area of the mandrel 2 is reduced so as to reduce the influence of heat on the material to be heated. The whole heat treatment is completed by moving the rectangular cylinder 1 from below to above at a constant speed and passing through the inside of the coil from above to below. The feeding speed of the rectangular cylinder 1 and the output of the high frequency power supply 5 were adjusted so that the heating temperature was 1300 ° C., 1200 ° C., the holding time was 20 seconds, and the holding time was 1100 ° C., and the holding time was 10 seconds. After completion of the heat treatment, a test piece having a width of 40 mm and a length of 40 mm was cut out, and the F value was measured by an X-ray diffraction method. Table 5 shows the measurement results. Parameter P is 3.26 for 1300 ° C, 1200 ° C
Is 3.05 and 1100 ° C. is 2.07.
【0063】[0063]
【表5】 [Table 5]
【0064】表に示すように(0002),(101
0)両面共に、F値はいずれも1/3となり、完全にラ
ンダムな結晶方位の配向となることが分かる。As shown in the table, (0002), (101)
0) On both surfaces, the F value is 1/3 in each case, indicating that the crystal orientation is completely random.
【0065】このものの高速中性子照射試験を行った結
果、3×1022n/cm2 でのひずみ量は約0.3×10
-4 以下ときわめて少ないものであった。また、このも
のの結晶粒径は各々100,150及び250μmであ
った。As a result of a high-speed neutron irradiation test, the strain amount at 3 × 10 22 n / cm 2 was about 0.3 × 10
It was extremely small, less than -4 . In addition, the crystal grain sizes of these were 100, 150 and 250 μm, respectively.
【0066】この熱処理を施した後、サンドブラスト処
理及び酸洗を行い、表面の酸化膜を除去した後、水蒸気
によるオートクレーブ処理が施される。After the heat treatment, sand blasting and pickling are performed to remove the oxide film on the surface, and then autoclave treatment with steam is performed.
【0067】図10は上述のように製作された角筒を使
用したBWR燃料集合体の部分断面図である。FIG. 10 is a partial cross-sectional view of a BWR fuel assembly using the rectangular tube manufactured as described above.
【0068】BWR燃料集合体は、図に示すように、多
数の燃料棒11とそれらを相互の所定の間隔で保持する
スペーサ12、更に、それらを収納する角筒のチャンネ
ルボックス1,燃料被覆管内に燃料ペレットが入った燃
料棒11の両端を保持する上部タイプレート14、及
び、下部タイプレート15、並びに、全体を搬送するた
めのハンドル13から構成される。As shown in the figure, the BWR fuel assembly is composed of a number of fuel rods 11, spacers 12 for holding them at a predetermined distance from each other, a rectangular channel box 1 for accommodating them, and a fuel cladding tube. An upper tie plate 14 and a lower tie plate 15 for holding both ends of a fuel rod 11 containing fuel pellets therein, and a handle 13 for transporting the whole.
【0069】また、これらの燃料集合体の製造に際して
は複雑な製造工程を経ており、各構造共に溶接で組立て
られる。Further, the production of these fuel assemblies goes through complicated production steps, and each structure is assembled by welding.
【0070】燃料チャンネルボックス1は燃料スペーサ
で組込まれた燃料棒11を内部に収納し、上部タイプレ
ート14と下部タイプレート15で燃料棒を固定した状
態で使用される。燃料チャンネルボックスは前述のよう
に二分割したコの字型板加工材をプラズマ溶接で接合し
た角筒形状を呈する。この部材はプラント運転時に燃料
棒で発生した高温水及び蒸気を強制的に上部に導く働き
をさせるものであり、角筒が外側に広がる応力が常時負
荷される状態で長時間使用される。The fuel channel box 1 is used in a state where the fuel rods 11 incorporated by the fuel spacers are accommodated therein, and the fuel rods are fixed by the upper tie plate 14 and the lower tie plate 15. As described above, the fuel channel box has a rectangular tube shape formed by joining two U-shaped plate-shaped workpieces by plasma welding. This member forcibly guides high-temperature water and steam generated from the fuel rods during operation of the plant to the upper portion, and is used for a long time in a state in which the stress that spreads the rectangular tube outward is constantly applied.
【0071】燃料集合体用チャンネルボックスは使用中
に高温高圧の炉水にさらされ、かつ、中性子照射を受け
る。また、角筒内部の圧力が外部に比べて高いため、内
圧を受ける。その結果、高温高圧環境下での耐食性,中
性子照射下での高いクリープ変形抵抗が要求される。The fuel assembly channel box is exposed to high-temperature and high-pressure reactor water during use and receives neutron irradiation. Further, since the pressure inside the rectangular tube is higher than that outside, the rectangular tube receives an internal pressure. As a result, corrosion resistance under high temperature and high pressure environment and high creep deformation resistance under neutron irradiation are required.
【0072】ジルコニウム基合金は、一般に、耐食性が
高く、中性子吸収断面積が小さい。これら特性は原子炉
用燃料集合体用材料として適しており、燃料集合体を構
成する燃料被覆管,チャンネルボックス1,スペーサ1
2等に使用される。使用される具体的なジルコニウム基
合金として、ジルカロイ−2(Sn1.2〜1.7wt
%,Fe0.07〜0.02wt%,Cr0.05〜0.1
5wt%,Ni0.03〜0.08wt%,残Zr )、
ジルカロイ−4(Sn1.2〜1.7wt%,Fe0.1
8〜0.24wt%,Cr0.05〜0.15wt%,残
Zr)、Zr−0.5〜2wt%Nb合金、Zr−2〜5
wt%Sn−0.5〜1.5wt%Nb−0.5〜1.5 w
t%Mo合金、Zr−0.5〜1.5wt%Sn−0.5
〜1.5wt%Nb−0.1〜1.0wt%Fe合金、Z
r−Nb(0.5〜5.0wt%)−Sn−(0〜3.0
wt% )−Fe,Ni,Cr,Ta,Pd,Mo,W
のいずれか1種(2wt%以下)合金等があり、いずれ
かの合金板に対しても本発明は効果が得られることが確
認された。A zirconium-based alloy generally has high corrosion resistance and a small neutron absorption cross-sectional area. These characteristics are suitable as a material for a fuel assembly for a nuclear reactor, and include a fuel cladding tube, a channel box 1, a spacer 1
2 and so on. As a specific zirconium-based alloy to be used, Zircaloy-2 (Sn 1.2 to 1.7 wt.
%, Fe 0.07 to 0.02 wt%, Cr 0.05 to 0.1
5 wt%, Ni 0.03-0.08 wt%, residual Zr),
Zircaloy-4 (Sn 1.2 to 1.7 wt%, Fe 0.1
8 to 0.24 wt%, Cr 0.05 to 0.15 wt%, remaining Zr), Zr-0.5 to 2 wt% Nb alloy, Zr-2 to 5
wt% Sn-0.5-1.5 wt% Nb-0.5-1.5 w
t% Mo alloy, Zr-0.5-1.5wt% Sn-0.5
-1.5 wt% Nb-0.1-1.0 wt% Fe alloy, Z
r-Nb (0.5-5.0 wt%)-Sn- (0-3.0
wt%)-Fe, Ni, Cr, Ta, Pd, Mo, W
(2% by weight or less), and it has been confirmed that the present invention is effective for any alloy plate.
【0073】前述のジルカロイ合金は沸騰水型原子炉中
で被覆管チャンネルボックス,スペーサに使用される
が、特に、被覆管は局部酸化(ノジュラ腐食)が発生し
易いので、最終冷間加工の前で、最終熱間加工後の間の
いずれかで外表面にのみα+β相又はβ相での焼入れを
施すのが好ましい。特に、最初の冷間加工前に焼入れす
るのが好ましい。焼入れにおける加熱温度は825〜1
100℃が好ましく、加熱時間は1分以内で3〜30秒
が好ましい。The above-mentioned zircaloy alloy is used in cladding channel boxes and spacers in a boiling water reactor. In particular, cladding tubes are apt to undergo local oxidation (nodular corrosion). It is preferable to quench the α + β phase or β phase only on the outer surface either during the final hot working or after the final hot working. In particular, quenching is preferably performed before the first cold working. The heating temperature during quenching is 825 to 1
The temperature is preferably 100 ° C., and the heating time is preferably 1 minute to 3 to 30 seconds.
【0074】加熱は誘導コイルによって連続的に行うの
がよく、冷却は加熱に続いて噴水を用いて行うのがよ
い。また管内に水を流しながら加熱するのもよい。ま
た、被覆管は管表面に対して垂直方向の〈0001〉方
位がFr値として0.66 以上とするのが好ましい。そ
の焼入れは結晶方位がランダムにならないように温度と
時間とがコントロールされる。Nbを含むジルコニウム
−ニオブ合金は、強度が高く、クリープ特性に優れ、水
素吸収率が低く、ノジュラ腐食と呼ばれる局部腐食も発
生しない。これらは、燃料集合体部材用材料として好ま
しい特性であるが、溶接部及び熱影響部の腐食が加速さ
れ剥離性の厚い白色酸化物を形成し易い。The heating is preferably performed continuously by an induction coil, and the cooling is preferably performed using a fountain following the heating. It is also possible to heat while flowing water in the tube. The cladding preferably has a <0001> orientation perpendicular to the tube surface having a Fr value of 0.66 or more. In the quenching, the temperature and time are controlled so that the crystal orientation does not become random. A zirconium-niobium alloy containing Nb has high strength, excellent creep characteristics, low hydrogen absorption rate, and does not cause local corrosion called nodular corrosion. These are preferable characteristics as a material for a fuel assembly member, but the corrosion of the welded portion and the heat-affected zone is accelerated, and a white oxide having a large peeling property is easily formed.
【0075】なお、ニオブ−ジルコニウム系多元合金と
して、0.5〜2.0wt%のNbと、1.5 重量%まで
のSnと、Fe,Cr,Mo,V,Cu,Ni及びWか
らなる群から選択された0.25wt% までの第三合金
元素を含むジルコニウム合金は高温蒸気環境内で耐食性
を有する特殊なミクロ構造をもつ。The niobium-zirconium multicomponent alloy is composed of 0.5 to 2.0 wt% of Nb, up to 1.5 wt% of Sn, and Fe, Cr, Mo, V, Cu, Ni and W. Zirconium alloys containing up to 0.25 wt% of a third alloy element selected from the group have a special microstructure that is resistant to corrosion in high temperature steam environments.
【0076】これらの合金を用いた本発明のチャンネル
ボックスは前述のように(0002),(1010)の両
面ともにF値を各々1/3になるように加熱保持され、
急冷することによって得られる。その結果、燃焼度32
GWd/t以上のものは勿論、45GWd/t以上のも
のに使用することが出来るとともに、表面に付着したク
ラッドを除くとともに燃料を取替えて再度使用する2サ
イクル用に使用可能であり、変形が少ないため炉心での
使用位置も前と同じ位置で使用可能とする。また、ジル
カロイ合金に限らず前述の合金からなる被覆管に対して
も前述の熱処理及び配向性を施すのがよい。As described above, the channel box of the present invention using these alloys is heated and held so that the F value on both sides of (0002) and (1010) becomes 1/3 each.
Obtained by quenching. As a result, the burnup 32
It can be used not only for GWd / t or more, but also for 45 GWd / t or more, and can be used for two cycles in which the clad attached to the surface is removed, fuel is replaced, and the fuel is used again, and there is little deformation. Therefore, it can be used at the same position as before in the core. The heat treatment and the orientation described above are preferably performed not only on the zircaloy alloy but also on the cladding tube made of the above-mentioned alloy.
【0077】被覆管及びチャンネルボックスともいずれ
も焼入を施したものを使用することにより全体として優
れたものが得られる。By using a quenched tube for both the cladding tube and the channel box, an excellent tube as a whole can be obtained.
【0078】[0078]
【発明の効果】以上説明した様に、本発明によれば、燃
料集合体ジルコニウム部材の結晶方位をランダム化出来
るので中性子照射量が1022(n/cm2 )を超える高照
射環境下で使用しても、照射成長、照射成長に起因する
曲がり変形が生じない。その結果、燃料集合体ジルコニ
ウム部材の長期間使用が可能となり、使用済み燃料廃棄
物低減に寄与できる。また、耐食性も向上し燃料集合体
ジルコニウム部材の信頼性向上に寄与できる。As described above, according to the present invention, the crystal orientation of the fuel assembly zirconium member can be randomized, so that it can be used in a high irradiation environment where the neutron irradiation dose exceeds 10 22 (n / cm 2 ). However, irradiation growth and bending deformation caused by irradiation growth do not occur. As a result, the fuel assembly zirconium member can be used for a long period of time, which can contribute to a reduction in spent fuel waste. Further, the corrosion resistance is also improved, which can contribute to the improvement of the reliability of the fuel assembly zirconium member.
【図1】本発明板の結晶方位の配向を示す模式図。FIG. 1 is a schematic view showing the orientation of the crystal orientation of a plate of the present invention.
【図2】照射成長の機構を示す模式図。FIG. 2 is a schematic diagram showing a mechanism of irradiation growth.
【図3】照射成長ひずみに及ぼす高速中性子照射量、並
びにFr値の影響を示す線図。FIG. 3 is a diagram showing the effects of fast neutron irradiation dose and Fr value on irradiation growth strain.
【図4】照射成長ひずみとFr値との関係を示す線図。FIG. 4 is a diagram showing the relationship between irradiation growth strain and Fr value.
【図5】Fr値とβZr結晶粒との相関係を示す線図。FIG. 5 is a diagram showing a phase relationship between an Fr value and βZr crystal grains.
【図6】照射成長ひずみとZr結晶粒径との関係を示す
線図。FIG. 6 is a diagram showing the relationship between irradiation growth strain and Zr crystal grain size.
【図7】照射成長ひずみとパラメータPとの関係を示す
線図。FIG. 7 is a diagram showing a relationship between irradiation growth strain and a parameter P.
【図8】Fr値に及ぼす温度と保持時間の関係を示す線
図。FIG. 8 is a diagram showing the relationship between the temperature and the holding time exerted on the Fr value.
【図9】チャンネルボックスの製造方法を示す装置の構
成図。FIG. 9 is a configuration diagram of an apparatus showing a method of manufacturing a channel box.
【図10】燃料集合体の部分断面図。FIG. 10 is a partial cross-sectional view of the fuel assembly.
1…チャンネルボックス、2…マンドル、3…ネジ、4
…高周波誘導加熱コイル、5…高周波電源、6…水吹き
付けノズル、7…溶接部、11…燃料棒、12…スペー
サ、13…ハンドル、14…上部タイプレート、15…
下部タイプレート。1 ... channel box, 2 ... mandrel, 3 ... screw, 4
... high frequency induction heating coil, 5 ... high frequency power supply, 6 ... water spray nozzle, 7 ... welded part, 11 ... fuel rod, 12 ... spacer, 13 ... handle, 14 ... upper tie plate, 15 ...
Lower tie plate.
フロントページの続き (51)Int.Cl.6 識別記号 庁内整理番号 FI 技術表示箇所 G21C 3/324 GDB 8719−4K C22F 1/00 682 // C22F 1/00 606 8719−4K 691B 623 8719−4K 691C 641 8719−4K 692A 682 G21C 3/06 N 691 J 3/30 V 692 GDBH (72)発明者 木田 利孝 茨城県日立市久慈町4026番地 株式会社日 立製作所日立研究所内 (72)発明者 大中 紀之 茨城県日立市久慈町4026番地 株式会社日 立製作所日立研究所内 (72)発明者 石崎 英昭 茨城県日立市幸町三丁目1番1号 株式会 社日立製作所日立工場内 (72)発明者 平川 博将 茨城県日立市幸町三丁目1番1号 株式会 社日立製作所日立工場内 (72)発明者 牧 英夫 茨城県日立市幸町三丁目1番1号 株式会 社日立製作所日立工場内Continuation of the front page (51) Int.Cl. 6 Identification number Agency reference number FI Technical display location G21C 3/324 GDB 8719-4K C22F 1/00 682 // C22F 1/00 606 8719-4K 691B 623 8719-4K 691C 641 8719-4K 692A 682 G21C 3/06 N 691 J 3/30 V 692 GDBH (72) Inventor Toshitaka Kida 4026 Kuji-cho, Hitachi City, Ibaraki Pref. Hitachi Research Laboratory, Hitachi, Ltd. (72) Onaka Inventor Nori No. 4026 Kuji-cho, Hitachi City, Ibaraki Prefecture Hitachi Research Laboratories, Hitachi, Ltd. (72) Inventor Hideaki Ishizaki 3-1-1, Kochimachi, Hitachi City, Ibaraki Prefecture Hitachi Plant, Ltd.Hitachi Plant (72) Inventor Hirakawa Hiromasa 3-1-1, Kochi-cho, Hitachi-shi, Ibaraki Pref. Hitachi, Ltd., Hitachi Plant (72) Inventor Hideo Maki 3-1-1, Kochi-cho, Hitachi, Hitachi, Ibaraki Pref., Hitachi, Ltd.
Claims (19)
以下を含有し、90重量%以上のZrを有するジルコニ
ウム基合金板において、該合金の六方晶Zrの〈0001〉
結晶方位の板表面に対する垂直方向への配向率(Fr
値)が0.20〜0.50であることを特徴とする低照射
成長ジルコニウム基合金板。(1) less than 5% by weight of Sn and / or 5% by weight of Nb
In a zirconium-based alloy plate containing the following and having 90% by weight or more of Zr, <0001> of hexagonal Zr of the alloy is used.
Orientation rate of crystal orientation in the direction perpendicular to the plate surface (Fr
Value) is 0.20 to 0.50.
以下を含有し、90重量%以上のZrを有するジルコニ
ウム基合金角形筒状部材において、該合金の六方晶Zr
の〈0001〉結晶方位の筒状部材表面に対する垂直方
向への配向率(Fr値)が0.25〜0.50、筒状部材
の長手方向への配向率(Ft)が0.25〜0.36及び
円周方向への配向率(Fl)が0.25〜0.36である
ことを特徴とする低照射成長ジルコニウム基合金角形筒
状部材。2. Sn 5% by weight or less and / or Nb 5% by weight.
A zirconium-based alloy prismatic tubular member having at least 90% by weight of Zr, comprising:
Of <0001> crystal orientation in the direction perpendicular to the surface of the cylindrical member (Fr value) is 0.25 to 0.50, and the orientation ratio (Ft) in the longitudinal direction of the cylindrical member is 0.25 to 0. A low-irradiation-grown zirconium-based alloy prismatic cylindrical member having a .36 and a circumferential orientation ratio (Fl) of 0.25 to 0.36.
以下を含有し、90重量%以上のZrを有するジルコニ
ウム基合金板において、該合金の結晶粒径が50〜50
0μmであることを特徴とする低照射成長ジルコニウム
基合金板。3. Sn 5% by weight or less and / or Nb 5% by weight.
In a zirconium-based alloy plate containing the following and having 90% by weight or more of Zr, the alloy has a crystal grain size of 50 to 50:
A low-irradiation-grown zirconium-based alloy plate having a thickness of 0 μm.
以下を含有し、90重量%以上のZrを有するジルコニ
ウム基合金板において、該合金の六方晶Zrの〈0001〉
結晶方位が実質的にランダムに配向し、1022n/cm2
以上の中性子照射成長によるひずみが3×10-4以下で
あることを特徴とする低照射成長ジルコニウム基合金
板。4. Sn 5% by weight or less and / or Nb 5% by weight.
In a zirconium-based alloy plate containing the following and having 90% by weight or more of Zr, <0001> of hexagonal Zr of the alloy is used.
The crystal orientation is substantially randomly oriented and 10 22 n / cm 2
A low-irradiation-grown zirconium-based alloy plate, wherein the strain due to the neutron irradiation growth is 3 × 10 −4 or less.
以下及び、90重量%以上のZrを有するジルコニウム
基合金板において、該合金の六方晶Zrの〈0001〉
結晶方位の板表面に対する垂直方向への配向率(Fr
値)が0.20〜0.50であることを特徴とする低照射
成長ジルコニウム基合金板。5. Sn 5% by weight or less and / or Nb 5% by weight.
In the following, and in a zirconium-based alloy plate having 90% by weight or more of Zr, <0001> of hexagonal Zr of the alloy is used.
Orientation rate of crystal orientation in the direction perpendicular to the plate surface (Fr
Value) is 0.20 to 0.50.
に加熱し、冷却するジルコニウム基合金板の製造法にお
いて、該合金の六方晶Zrの〈0001〉結晶方位の板
表面に対する垂直方向への配向率(Fr値)が0.20
〜0.50となるように前記β相単相温度領域にて加熱
保持後急冷する工程を有することを特徴とする低照射成
長ジルコニウム基合金板の製造法。6. A method for producing a zirconium-based alloy sheet in which a zirconium-based alloy sheet is heated to a β-phase single-phase temperature region and cooled, wherein the <0001> crystal orientation of hexagonal Zr of the alloy is perpendicular to the plate surface. Has an orientation ratio (Fr value) of 0.20
A method of producing a low-irradiation-grown zirconium-based alloy plate, comprising a step of heating and holding in the β-phase single-phase temperature region and rapidly cooling the mixture so as to be 0.50 to 0.50.
に加熱し、冷却するジルコニウム基合金板の製造法にお
いて、前記β相単相温度領域での加熱を次式によって求
められるパラメータPの値が0.8 〜5となるように保
持し、急冷する工程を有することを特徴とする低照射成
長ジルコニウム基合金板の製造法。 P=logt×log(T−980) (t:加熱時間(秒),T:加熱温度(℃))7. A method for producing a zirconium-based alloy plate in which a zirconium-based alloy plate is heated to a β-phase single-phase temperature region and cooled, wherein the heating in the β-phase single-phase temperature region is a parameter P obtained by the following equation. A method for producing a low-irradiation-grown zirconium-based alloy sheet, comprising a step of maintaining the value to be 0.8 to 5 and rapidly cooling. P = logt × log (T-980) (t: heating time (second), T: heating temperature (° C.))
にβ相単相温度領域に誘導加熱によって相対的に移動さ
せながら連続的に加熱するとともに該加熱された部分を
冷媒によって強制的に冷却するジルコニウム基合金角形
筒状部材の製造法において、前記合金の六方晶Zrの
〈0001〉結晶方位の筒状部材表面に対する垂直方向
への配向率(Fr値)が0.20〜0.50となるように
前記β相単相温度領域にて加熱保持後急冷する工程を有
することを特徴とする低照射成長ジルコニウム基合金角
形筒部材の製造法。8. A heating method for continuously heating a zirconium-based alloy rectangular cylindrical member locally to a β-phase single-phase temperature region by induction heating, and forcibly cooling the heated portion by a refrigerant. The hexagonal Zr of the alloy has an orientation ratio (Fr value) of the <0001> crystal orientation in a direction perpendicular to the surface of the cylindrical member, which is 0.20 to 0.50. A method of producing a low-irradiation-grown zirconium-based alloy prismatic cylindrical member, characterized by comprising a step of rapidly cooling after heating and holding in the β-phase single-phase temperature region.
部材からなる燃料チャンネルボックスにおいて、前記合
金の六方晶Zrの〈0001〉結晶方位の筒状部材表面
に対する垂直方向への配向率(Fr値)が0.20〜0.
50であることを特徴とする燃料チャンネルボックス。9. A fuel channel box made of a rectangular cylindrical member made of a zirconium-based alloy member, wherein the hexagonal Zr of the alloy has a <0001> crystal orientation in a direction perpendicular to the surface of the cylindrical member (Fr value). Is 0.20 to 0.2.
50. A fuel channel box, wherein the number is 50.
燃料棒、該燃料棒を複数本収納するジルコニウム基合金
よりなる燃料チャンネルボックス、該チャンネルボック
ス内の前記燃料棒の間を仕切るスペーサ、前記チャンネ
ルボックスの上部及び下部に設けられた上部格子板及び
下部格子板を備えた燃料集合体において、前記合金の六
方晶Zrの〈0001〉結晶方位の板表面に対する垂直
方向への配向率(Fr値)が0.20〜0.50であること
を特徴とする燃料集合体。10. A fuel rod containing a fuel pellet in a fuel cladding tube, a fuel channel box made of a zirconium-based alloy for accommodating a plurality of the fuel rods, a spacer separating the fuel rods in the channel box, and the channel. In a fuel assembly including an upper lattice plate and a lower lattice plate provided at the upper and lower parts of a box, the orientation ratio of the <0001> crystal orientation of the hexagonal Zr of the alloy in the direction perpendicular to the plate surface (Fr value) Is from 0.20 to 0.50.
ウム基合金からなるチャンネルボックスの使用方法にお
いて、前記合金は1022n/cm2 以上での中性子照射成
分によるひずみが3×10-4以下であり、少なくとも1
回原子燃料を取替えて使用することを特徴とする原子燃
料チャンネルボックスの使用方法。11. A method of using a channel box made of a zirconium-based alloy in which a plurality of nuclear fuel rods are arranged, wherein said alloy has a strain of 10 × 22 n / cm 2 or more and a neutron irradiation component of 3 × 10 −4 or less. And at least one
A method of using a nuclear fuel channel box, wherein the nuclear fuel is replaced and used.
なる燃料チャンネルボックスの使用方法において、前記
合金は1022n/cm2 以上での中性子照射成分によるひ
ずみが3×10-4以下であり、取出燃焼度32GWd/
t以上又は少なくとも1回原子燃料を交換して使用する
ことを特徴とする燃料チャンネルボックスの使用方法。12. A method of using a fuel channel box comprising a cylindrical member made of a zirconium-based alloy member, wherein the alloy has a strain of 3 × 10 −4 or less due to a neutron irradiation component at 10 22 n / cm 2 or more, Removal burnup 32 GWd /
A method for using a fuel channel box, wherein the fuel is exchanged and used at least once or at least once.
燃料棒、該燃料棒を複数本収納し、ジルコニウム基合金
からなるチャンネルボックス、該チャンネルボックス内
の前記燃料棒の間を仕切るスペーサ、前記チャンネルボ
ックスの上部及び下部に設けられた上部格子板及び下部
格子板を備えた燃料集合体の使用方法において、該合金
の六方晶Zrの〈0001〉結晶方位の板表面に対する
垂直方向への配向率(Fr値)が0.20〜0.50あ
り、取出燃焼度32GWd/t以上又は少なくとも1回
原子燃料を取替えて使用することを特徴とする燃料集合
体の使用方法。13. A fuel rod containing a fuel pellet in a fuel cladding tube, a plurality of fuel rods housed therein, a channel box made of a zirconium-based alloy, a spacer separating the fuel rods in the channel box, and the channel. In a method of using a fuel assembly including an upper lattice plate and a lower lattice plate provided at an upper part and a lower part of a box, an orientation ratio of a <0001> crystal orientation of hexagonal Zr of the alloy in a direction perpendicular to a plate surface ( (Fr value) is 0.20 to 0.50, and the removed burnup is 32 GWd / t or more, or at least once, the nuclear fuel is replaced and used.
ウム基合金からなるチャンネルボックスの使用方法にお
いて、前記合金は1022n/cm2 以上での中性子照射成
分によるひずみが3×10-4以下であり、取出燃焼度3
2GWd/t以上又は中性子照射量で1022n/cm以上
受ける期間使用することを特徴とするチャンネルボック
スの使用方法。14. A method of using a channel box made of a zirconium-based alloy in which a plurality of nuclear fuel rods are arranged, wherein the alloy has a strain of 10 22 n / cm 2 or more and a neutron irradiation component of 3 × 10 -4 or less. And withdrawal burnup of 3
A method of using a channel box, wherein the channel box is used for a period of 2 GWd / t or more or a neutron irradiation dose of 10 22 n / cm or more.
りなる複数の原子燃料チャンネルボックスを備え、所定
期間運転後に燃料を取換え、引き続いて所定期間運転す
る原子炉の運転方法において、前記合金は1022n/cm
2 以上の中性子照射成長によるひずみが3×10-4以下
であり、取出燃焼度32GWd/t以上の運転又は前記
後の運転時の前記チャンネルボックスの位置を前の運転
時の位置と同じに配置して少なくとも1回燃料を取替え
て運転することを特徴とする原子炉の運転方法。15. A method for operating a nuclear reactor, comprising: a plurality of nuclear fuel channel boxes formed of a cylinder of a zirconium-based alloy in a reactor core; replacing fuel after a predetermined period of operation; and subsequently operating for a predetermined period of time. Is 10 22 n / cm
The strain caused by the neutron irradiation growth of 2 or more is 3 × 10 −4 or less, and the position of the channel box at the time of operation with an extraction burnup of 32 GWd / t or more or after the operation is the same as the position at the time of the previous operation. And operating at least once by replacing fuel.
%以下を含有し、90重量%以上のZrを有する燃料チ
ャンネルボックスにおいて、前記合金の六方晶Zrの
〈0001〉結晶方位の板表面に対する垂直方向への配
向率(Fr値)が0.20〜0.50 であることを特徴と
する燃料チャンネルボックス。16. A fuel channel box containing 5% by weight of Sn and / or 5% by weight of Nb and having Zr of 90% by weight or more, wherein the <0001> crystal orientation of hexagonal Zr of the alloy is perpendicular to the plate surface. A fuel channel box having an orientation ratio (Fr value) in a direction of 0.20 to 0.50.
%以下を含有し、90重量%以上のZrを有するジルコ
ニウム基合金板製角形筒状部材からなる燃料チャンネル
ボックスにおいて、該合金の六方晶Zrの〈0001〉
結晶方位の筒状部材表面に対する垂直方向への配向率
(Fr値)が0.25〜0.50、筒状部材の長手方向へ
の配向率(Ft)が0.25〜0.36及び円周方向への
配向率(Fl)が0.25〜0.36 であることを特徴とす
る燃料チャンネルボックス。17. A fuel channel box comprising a square cylindrical member made of a zirconium-based alloy plate containing 5% by weight of Sn and / or 5% by weight of Nb and having Zr of 90% by weight or more. <0001>
The orientation ratio (Fr value) of the crystal orientation in the direction perpendicular to the surface of the tubular member (Fr value) is 0.25 to 0.50, the orientation ratio (Ft) in the longitudinal direction of the tubular member is 0.25 to 0.36, and a circle. A fuel channel box having a circumferential orientation ratio (Fl) of 0.25 to 0.36.
%以下を含有し、90重量%以上のZrを有するジルコ
ニウム基合金板製角形筒状部材からなる燃料チャンネル
ボックスにおいて、前記合金はその六方晶Zrの〈00
01〉結晶方位の筒状部材表面に対する垂直方向への配
向率(Fr値)が0.20〜0.50であり、その結晶粒
径が50〜500μmであることを特徴とする燃料チャ
ンネルボックス。18. A fuel channel box comprising a rectangular cylindrical member made of a zirconium-based alloy plate containing 5% by weight of Sn and / or 5% by weight of Nb and having Zr of 90% by weight or more, wherein the alloy is a hexagonal crystal. Zr <00
<01> A fuel channel box characterized in that the crystal orientation has an orientation ratio (Fr value) in a direction perpendicular to the surface of the cylindrical member of 0.20 to 0.50 and a crystal grain size of 50 to 500 µm.
なる燃料チャンネルボックスにおいて、前記合金はその
六方晶Zrの〈0001〉結晶方位が実質的にランダム
に配向し、1022n/cm2 以上の中性子照射成長による
ひずみが3×10-4以下であることを特徴とする燃料チ
ャンネルボックス。19. A fuel channel box comprising a rectangular cylindrical member made of a zirconium-based alloy, wherein said alloy has a <0001> crystal orientation of hexagonal Zr which is substantially randomly oriented, and is not less than 10 22 n / cm 2 . A fuel channel box, wherein a strain due to neutron irradiation growth is 3 × 10 −4 or less.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP10128297A JP3492881B2 (en) | 1997-04-18 | 1997-04-18 | Fuel channel box and fuel assembly |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP10128297A JP3492881B2 (en) | 1997-04-18 | 1997-04-18 | Fuel channel box and fuel assembly |
Related Parent Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP03314294A Division JP3082369B2 (en) | 1990-11-28 | 1991-11-28 | Method of manufacturing fuel channel box and method of manufacturing and using fuel assembly |
Publications (2)
Publication Number | Publication Date |
---|---|
JPH1036929A true JPH1036929A (en) | 1998-02-10 |
JP3492881B2 JP3492881B2 (en) | 2004-02-03 |
Family
ID=14296513
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP10128297A Expired - Lifetime JP3492881B2 (en) | 1997-04-18 | 1997-04-18 | Fuel channel box and fuel assembly |
Country Status (1)
Country | Link |
---|---|
JP (1) | JP3492881B2 (en) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CZ309191B6 (en) * | 2020-12-08 | 2022-04-27 | Univerzita Karlov | High-strength zirconium alloy and processing it |
-
1997
- 1997-04-18 JP JP10128297A patent/JP3492881B2/en not_active Expired - Lifetime
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CZ309191B6 (en) * | 2020-12-08 | 2022-04-27 | Univerzita Karlov | High-strength zirconium alloy and processing it |
Also Published As
Publication number | Publication date |
---|---|
JP3492881B2 (en) | 2004-02-03 |
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