JPH04329855A - Production of zirconium alloy - Google Patents
Production of zirconium alloyInfo
- Publication number
- JPH04329855A JPH04329855A JP14647391A JP14647391A JPH04329855A JP H04329855 A JPH04329855 A JP H04329855A JP 14647391 A JP14647391 A JP 14647391A JP 14647391 A JP14647391 A JP 14647391A JP H04329855 A JPH04329855 A JP H04329855A
- Authority
- JP
- Japan
- Prior art keywords
- zirconium alloy
- cold working
- corrosion resistance
- creep deformation
- 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.)
- Withdrawn
Links
- 229910001093 Zr alloy Inorganic materials 0.000 title claims abstract description 33
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 18
- 238000005482 strain hardening Methods 0.000 claims abstract description 30
- 230000032683 aging Effects 0.000 claims abstract description 12
- 238000000034 method Methods 0.000 claims description 11
- 230000007797 corrosion Effects 0.000 abstract description 34
- 238000005260 corrosion Methods 0.000 abstract description 34
- 229910001257 Nb alloy Inorganic materials 0.000 abstract description 10
- 230000002542 deteriorative effect Effects 0.000 abstract description 5
- 239000000243 solution Substances 0.000 description 9
- XLYOFNOQVPJJNP-ZSJDYOACSA-N Heavy water Chemical compound [2H]O[2H] XLYOFNOQVPJJNP-ZSJDYOACSA-N 0.000 description 8
- 238000012360 testing method Methods 0.000 description 6
- 238000011156 evaluation Methods 0.000 description 5
- 239000000463 material Substances 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 4
- 238000010586 diagram Methods 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- 230000000694 effects Effects 0.000 description 3
- 238000010438 heat treatment Methods 0.000 description 3
- 238000001125 extrusion Methods 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Chemical compound O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 description 1
- 238000010521 absorption reaction Methods 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 238000005253 cladding Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 239000003758 nuclear fuel Substances 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000011084 recovery Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 230000035882 stress Effects 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Landscapes
- Heat Treatment Of Steel (AREA)
Abstract
Description
【０００１】0001
【産業上の利用分野】本発明は型ジルコニウム合金の製
造方法に関し、さらに詳しくは、（α＋β）型ジルコニ
ウム合金製圧力管および燃料被覆管等の原子炉用炉芯部
材として使用することができる溶体化処理後、時効処理
を行って使用する（α＋β）型ジルコニウム合金の製造
方法に関するものである。[Industrial Application Field] The present invention relates to a method for manufacturing a type zirconium alloy, and more specifically, a solution that can be used as a core member for a nuclear reactor such as a pressure tube or a fuel cladding tube made of an (α+β) type zirconium alloy. The present invention relates to a method for manufacturing an (α+β) type zirconium alloy that is used after being subjected to aging treatment after chemical treatment.
【０００２】0002
【従来技術】一般に、（α＋β）型ジルコニウム合金は
、優れた耐蝕性を有しており、かつ、中性子吸収断面積
が小さいという特性に、さらに、加工性にも優れている
こということは、従来よりよく知られているところであ
る。[Prior Art] In general, (α+β) type zirconium alloys have excellent corrosion resistance and a small neutron absorption cross section, and are also excellent in workability. This is something that has been well known for some time.
【０００３】また、（α＋β）型ジルコニウム合金は、
原子炉用炉芯部材として広く使用されているα型ジルコ
ニウム合金、即ち、ジルカロイ−２およびジルカロイ−
４と比較して、機械的強度が高いことから、特に、高強
度が要求されている重水型原子炉の炉芯部材の、圧力管
材料等に使用されている。[0003] Furthermore, the (α+β) type zirconium alloy is
α-type zirconium alloys, namely Zircaloy-2 and Zircaloy-2, are widely used as core members for nuclear reactors.
Since it has higher mechanical strength than No. 4, it is particularly used as pressure pipe material for core members of heavy water reactors, which require high strength.
【０００４】このような（α＋β）型ジルコニウム合金
は、基となるジルコニウムにβ安定化元素であるＮｂを
約２．６ｗｔ％含有させたＺｒ−２．５ｗｔ％Ｎｂで示
される。Such an (α+β) type zirconium alloy is represented by Zr-2.5wt%Nb, which is a base zirconium containing about 2.6wt% of Nb, which is a β-stabilizing element.
【０００５】そして、現在、Ｚｒ−２．５ｗｔ％Ｎｂ合
金製重水型原子炉用圧力管を製造する場合には、図１に
示すような工程により行われている。[0005]Currently, when manufacturing a pressure tube for a heavy water nuclear reactor made of a Zr-2.5wt%Nb alloy, a process as shown in FIG. 1 is carried out.
【０００６】図１の製造工程の内で、機械的強度を支配
するとされている工程は、溶体化処理工程の温度を高く
することにより、強度が向上することはよく知られてい
ることである。It is well known that in the manufacturing process shown in FIG. 1, the strength is improved by increasing the temperature of the solution treatment process, which is said to control the mechanical strength. .
【０００７】また、溶体化処理後の冷間加工および時効
処理は耐蝕性に影響を与える工程であり、冷間加工率を
１０〜２０％と大きくとり、また、時効処理温度を高く
することにより、耐蝕性が向上することもよく知られて
いる。[0007] Furthermore, cold working and aging treatment after solution treatment are processes that affect corrosion resistance. It is also well known that corrosion resistance is improved.
【０００８】上記のようにして製造されたＺｒ−２．５
ｗｔ％Ｎｂ合金は、機械的強度が向上すると共に、ノジ
ュラー腐蝕等の局部腐蝕の発生することはないものと考
えられている。Zr-2.5 produced as described above
It is thought that the wt% Nb alloy has improved mechanical strength and does not cause localized corrosion such as nodular corrosion.
【０００９】しかし、重水型原子炉用圧力管等の高圧下
において使用される炉芯部材としての用途に対しては、
高い耐蝕性および高い機械的強度を有しているだけでは
不充分である。However, for use as reactor core members used under high pressure such as pressure pipes for heavy water reactors,
It is not sufficient to have high corrosion resistance and high mechanical strength.
【００１０】即ち、上記に説明した圧力管等の炉芯部材
は、その使用中に常に１５０気圧程度の内圧が負荷され
ているので、クリープ変形を起こすことがある。この変
形が原子燃料の高燃焼度化および運転期間の長期化の障
害になることから、耐クリープ変形性を向上させること
は不可欠の事とされている。That is, since the furnace core members such as the pressure tubes described above are constantly loaded with an internal pressure of about 150 atmospheres during use, creep deformation may occur. Since this deformation becomes an obstacle to increasing the burnup of nuclear fuel and prolonging its operating period, it is considered essential to improve the creep deformation resistance.
【００１１】この耐クリープ変形性を向上させることは
、機械的強度および耐蝕性を劣化させることなく、換言
すれば、高強度、高耐蝕性および高耐クリープ変形性を
兼ね備えることも必要条件である。[0011] Improving this creep deformation resistance is a necessary condition without deteriorating mechanical strength and corrosion resistance, in other words, it is also necessary to have high strength, high corrosion resistance, and high creep deformation resistance. .
【００１２】しかしながら、β安定化元素を含有する（
α＋β）型Ｚｒ−２．５ｗｔ％Ｎｂ合金については、高
強度、高耐蝕性を保持し、かつ、高耐クリープ変形性を
向上させるための技術に関する文献および提案等につい
ては殆ど存在していないのが現状である。However, the β-stabilizing element (
Regarding the α+β) type Zr-2.5wt%Nb alloy, there are almost no documents or proposals regarding techniques for maintaining high strength, high corrosion resistance, and improving high creep deformation resistance. is the current situation.
【００１３】[0013]
【発明が解決しようとする課題】本発明は上記に説明し
た従来の重水型原子炉用圧力管等の炉芯部材に使用され
る（α＋β）型Ｚｒ−２．５ｗｔ％Ｎｂ合金の種々の問
題点に鑑み、本発明者が鋭意研究を行い、検討を重ねた
結果、（α＋β）型ジルコニウム合金の製造において、
耐蝕性、機械的強度を劣化させることなく、耐クリープ
変形性を向上させるために、溶体化処理後の冷間加工率
を厳密に制御することが重要であることを知見し、ジル
コニウム合金の製造方法を開発したのである。[Problems to be Solved by the Invention] The present invention solves various problems of the (α+β) type Zr-2.5wt%Nb alloy used in reactor core members such as pressure pipes for conventional heavy water nuclear reactors as explained above. In view of this, the present inventor conducted intensive research and as a result of repeated consideration, in the production of (α + β) type zirconium alloy,
We discovered that it is important to strictly control the cold working rate after solution treatment in order to improve creep deformation resistance without deteriorating corrosion resistance and mechanical strength, and we started manufacturing zirconium alloys. He developed a method.
【００１４】[0014]
【課題を解決するための手段】本発明に係るジルコニウ
ム合金の製造方法の特徴とするところは、（α＋β）型
ジルコニウム合金に対して溶体化処理を行った後、１％
〜５％未満の冷間加工を行い、次いで、時効処理を行う
ことにある。[Means for Solving the Problems] The feature of the method for producing a zirconium alloy according to the present invention is that after solution treatment is performed on an (α+β) type zirconium alloy, 1%
~5% cold working and then aging treatment.
【００１５】本発明に係るジルコニウム合金の製造方法
について、以下詳細に説明する。The method for producing a zirconium alloy according to the present invention will be explained in detail below.
【００１６】（α＋β）型ジルコニウム合金、即ち、Ｚ
ｒ−２．５ｗｔ％Ｎｂ合金は図１に示すように、溶体化
処理後、時効処理を行う前に、冷間加工が行われる。こ
の冷間加工は、溶体化処理により過飽和に固溶している
β安定元素であるＮｂの時効処理による析出を促進する
効果のあることはよく知られている。このような析出が
起こるとマトリックスの歪が小さくなり、これが耐蝕性
を向上させるのである。(α+β) type zirconium alloy, that is, Z
As shown in FIG. 1, the r-2.5 wt% Nb alloy is subjected to cold working after solution treatment and before aging treatment. It is well known that this cold working has the effect of accelerating the precipitation of Nb, which is a β-stable element, which has been dissolved in supersaturated solid solution during the solution treatment due to the aging treatment. When such precipitation occurs, the strain in the matrix is reduced, which improves corrosion resistance.
【００１７】図２に冷間加工と耐蝕性との関係について
示してあり、この図２から１％の冷間加工を行うことに
より耐蝕性が向上し、２０％までは変化のないことがわ
かる。 この図２は、４００℃、１０５ｋｇｆ／ｃｍ
２の水蒸気中で７２時間の腐蝕試験を行い、腐蝕増量（
ｍｇ／ｄｍ２）を評価したものである。[0017] Figure 2 shows the relationship between cold working and corrosion resistance, and it can be seen from Figure 2 that the corrosion resistance improves with 1% cold working and remains unchanged up to 20%. . This figure 2 shows the temperature at 400℃ and 105kgf/cm.
A corrosion test was conducted for 72 hours in water vapor of No. 2, and the corrosion increase (
mg/dm2).
【００１８】これは、従来の冷間加工率によって耐蝕性
のあまり変化しないジルカロイ−２およびジルカロイ−
４等のα型ジルコニウム合金とは、全く相違している（
α＋β）型ジルコニウム合金特有の挙動であり、即ち、
従来の（α＋β）ジルコニウム合金においては、冷間加
工率が大となる程、耐蝕性が向上するため冷間加工率を
１０〜２０％と高く設定しているものである。This is because the corrosion resistance of Zircaloy-2 and Zircaloy-2 does not change much depending on the conventional cold working rate.
It is completely different from α-type zirconium alloys such as No. 4 (
This is a behavior peculiar to α+β) type zirconium alloys, that is,
In conventional (α+β) zirconium alloys, the cold working rate is set as high as 10 to 20% because the corrosion resistance improves as the cold working rate increases.
【００１９】しかして、本発明に係るジルコニウム合金
の製造方法において、冷間加工率を１〜５％未満に限定
するものであり、冷間加工率が１％未満では時効処理を
行ってもＮｂの析出が起こらず優れた耐蝕性を期待する
ことができず、また、冷間加工率を１％以上とすること
により、Ｎｂの析出が促進されて耐蝕性が向上する。従
って、冷間加工率は１％以上で充分に耐蝕性を向上させ
ることができる。However, in the method for producing a zirconium alloy according to the present invention, the cold working rate is limited to less than 1% to less than 5%, and if the cold working rate is less than 1%, Nb will not be produced even after aging treatment. Since precipitation of Nb does not occur, excellent corrosion resistance cannot be expected, and by setting the cold working rate to 1% or more, precipitation of Nb is promoted and corrosion resistance is improved. Therefore, the corrosion resistance can be sufficiently improved with a cold working ratio of 1% or more.
【００２０】また、冷間加工率を５％未満とすることに
ついて説明すると、図３に示すように、冷間加工率とク
リープ変形との関係から設定される。即ち、図３よりク
リープ変形は冷間加工率が５％を越えると急激に増加す
る。これは、冷間加工率が５％を越えると蓄積された歪
のために回復が起こり、クリープ変形が促進されること
による。図３は、３０ｋｇｆ／ｍｍ２の応力を負荷して
、３５０℃の温度に加熱し、１２００時間経過後のクリ
ープ変形量（％／１２００時間）を評価したものである
。Further, to explain why the cold working rate is less than 5%, it is set based on the relationship between the cold working rate and creep deformation, as shown in FIG. That is, from FIG. 3, creep deformation increases rapidly when the cold working rate exceeds 5%. This is because when the cold working rate exceeds 5%, recovery occurs due to accumulated strain and creep deformation is promoted. FIG. 3 shows the evaluation of the amount of creep deformation (%/1200 hours) after 1200 hours of applying a stress of 30 kgf/mm2 and heating to a temperature of 350°C.
【００２１】従って、従来の（α＋β）型ジルコニウム
合金としてのＺｒ−２．５ｗｔ％Ｎｂ合金は、機械的強
度および耐蝕性を劣化させることなく耐クリープ変形性
を向上させるためには、冷間加工率を制御することが重
要であり、冷間加工率は１〜５％未満とする。Therefore, the Zr-2.5wt%Nb alloy, which is a conventional (α+β) type zirconium alloy, has to be cold-worked in order to improve its creep deformation resistance without deteriorating its mechanical strength and corrosion resistance. It is important to control the cold work rate and the cold work rate should be less than 1-5%.
【００２２】次に、重要な特性である強度について説明
すると、冷間加工率によって強度が変化することはなく
、即ち、図４に示すように、冷間加工率と機械的強度（
引張強度）の関係からわかるように、冷間加工率が１〜
２０％までは機械的強度に変化はない。このことは、こ
の冷間加工率の範囲内においては、時効処理により析出
したＮｂ析出物の引張強度への寄与が同じであることに
よる。図４は、ＪＩＳの引張試験条件に基づき引張強度
を評価したものである。Next, to explain strength, which is an important characteristic, strength does not change depending on the cold working rate. In other words, as shown in FIG. 4, the cold working rate and the mechanical strength (
As can be seen from the relationship between tensile strength and
There is no change in mechanical strength up to 20%. This is because within this range of cold working rates, the contribution of Nb precipitates precipitated by aging treatment to the tensile strength is the same. FIG. 4 shows the evaluation of tensile strength based on JIS tensile test conditions.
【００２３】[0023]
【実 施 例】本発明に係るジルコニウム合金の製
造方法について、実施例を説明する。[Example] Examples of the method for producing a zirconium alloy according to the present invention will be described.
【００２４】[0024]
【実 施 例 １】（α＋β）型Ｚｒ−２．５ｗｔ％Ｎ
ｂ合金を、通常の溶製法により溶解、鋳造後、１０ｍｍ
厚×１５０ｍｍ幅×２００ｍｍ長さの板材に加工を行っ
た。[Example 1] (α+β) type Zr-2.5wt%N
After melting and casting b alloy by normal melting method, 10mm
A plate material of thickness x 150 mm width x 200 mm length was processed.
【００２５】この板材に対して、８７０℃の温度に３０
分保持後水冷する溶体化処理を行い、さらに、この板材
に最大２０％の冷間加工を行った後、５００℃の温度に
２４時間保持後炉冷する時効処理を行った。[0025] This plate material was heated to a temperature of 870°C for 30 minutes.
After holding the plate for 24 hours and cooling it in a solution heat treatment, the plate material was subjected to cold working of up to 20%, and then subjected to an aging treatment in which it was held at a temperature of 500° C. for 24 hours and then cooled in a furnace.
【００２６】このような処理を行った板材から試験片を
採取して、下記に説明する試験を行った。
（１）２４時間腐蝕試験。
（２）引張試験。
（３）３５０℃×３０ｊｇｆ／ｍｍ２×１２００時間の
クリープ試験。
そして、耐蝕性、引張強度およびクリープ変形量を調査
した。
耐蝕性の評価
レベル１は腐蝕増量が３５ｍｇ／ｄｍ２未満，レベル２
は腐蝕増量が３５ｍｇ／ｄｍ２以上，クリープ変形量の
評価
レベル１はクリープ変形量が１％未満，レベル２はクリ
ープ変形量が１〜２％，レベル３はクリープ変形量が２
％以上，表１にこれらの試験結果を示してあるが、本発
明に係るジルコニウム合金の製造方法により製造された
ジルコニウム合金は、比較例に比して耐蝕性は殆ど変わ
らないが、しかし、クリープ変形量のレベルは１であり
、比較例のＧ〜Ｋのレベル２および３よりも優れている
ことがわかる。[0026] A test piece was taken from the plate material subjected to such treatment, and the test described below was conducted. (1) 24 hour corrosion test. (2) Tensile test. (3) Creep test at 350°C x 30jgf/mm2 x 1200 hours. Then, the corrosion resistance, tensile strength, and amount of creep deformation were investigated. Corrosion resistance evaluation level 1 is corrosion increase less than 35mg/dm2, level 2
The corrosion increase is 35mg/dm2 or more, creep deformation evaluation level 1 is less than 1% creep deformation, level 2 is creep deformation 1 to 2%, and level 3 is creep deformation 2%.
% or more, these test results are shown in Table 1. The zirconium alloy manufactured by the zirconium alloy manufacturing method according to the present invention has almost no difference in corrosion resistance compared to the comparative example, but has a creep resistance. It can be seen that the deformation amount level is 1, which is superior to levels 2 and 3 of G to K of the comparative examples.
【００２７】[0027]
【表１】[Table 1]
【００２８】[0028]
【実 施 例 ２】実施例１と同様な方法により、（α
＋β）型Ｚｒ−２．５ｗｔ％Ｎｂ合金丸棒を素材として
、外径１５０ｍｍの押出ビレットを作製し、加熱温度を
８５０℃に制御して押出を行った。[Example 2] Using a method similar to Example 1, (α
An extrusion billet with an outer diameter of 150 mm was prepared using a +β) type Zr-2.5wt% Nb alloy round bar as a raw material, and extrusion was performed while controlling the heating temperature to 850°C.
【００２９】さらに、加工率１０％の冷間加工を行った
後、８７０℃の温度に加熱し、直ちに水冷を行った。[0029] Furthermore, after performing cold working at a processing rate of 10%, it was heated to a temperature of 870°C and immediately cooled with water.
【００３０】その後、冷間加工率０％、１．０％、２．
３％、３．５％、４．９％、６％、１１．８％、１５．
２％で８種類の管を作製した。これらの管を５００℃×
２４時間の時効処理を行い、耐蝕性および耐クリープ変
形性を評価した。評価方法は実施例１の場合と同じであ
る。[0030] After that, the cold working rate is 0%, 1.0%, 2.
3%, 3.5%, 4.9%, 6%, 11.8%, 15.
Eight types of tubes were made at 2%. These tubes were heated to 500℃
Aging treatment was performed for 24 hours, and corrosion resistance and creep deformation resistance were evaluated. The evaluation method was the same as in Example 1.
【００３１】表２に製造工程を示す。また、表３に耐蝕
性、耐クリープ変形性および引張強度を示してある。こ
の表３から、本発明に係るジルコニウム合金の製造方法
により製造されたジルコニウム合金は、比較例に比して
耐蝕性、耐クリープ変形性に優れており、また、引張強
度も比較例と同等程度である。Table 2 shows the manufacturing process. Furthermore, Table 3 shows the corrosion resistance, creep deformation resistance, and tensile strength. From Table 3, the zirconium alloy manufactured by the method for manufacturing a zirconium alloy according to the present invention has superior corrosion resistance and creep deformation resistance compared to the comparative example, and also has a tensile strength comparable to that of the comparative example. It is.
【００３２】[0032]
【表２】[Table 2]
【００３３】[0033]
【表３】[Table 3]
【００３４】[0034]
【発明の効果】以上説明したように、本発明に係るジル
コニウム合金の製造方法は上記の構成を有しているもの
であるから、ジルコニウム合金の（α＋β）型Ｚｒ−２
．５ｗｔ％Ｎｂ合金において、溶体化処理後における冷
間加工率を厳密に制御することによって、機械的強度お
よび耐蝕性を劣化させることなく、耐クリープ変形性を
著しく向上させることができるジルコニウム合金が製造
できるという効果を有しているものである。Effects of the Invention As explained above, since the method for producing a zirconium alloy according to the present invention has the above-mentioned structure, the (α+β) type Zr-2 of the zirconium alloy
．． In a 5wt% Nb alloy, by strictly controlling the cold working rate after solution treatment, a zirconium alloy has been produced that can significantly improve creep deformation resistance without deteriorating mechanical strength and corrosion resistance. This has the effect that it can be done.
【図１】Ｚｒ−２．５ｗｔ％Ｎｂ合金の製造工程を示す
図である。FIG. 1 is a diagram showing the manufacturing process of Zr-2.5wt%Nb alloy.
【図２】冷間加工率と耐蝕性との関係を示す図である。FIG. 2 is a diagram showing the relationship between cold working rate and corrosion resistance.
【図３】冷間加工率とクリープ変形の関係を示す図であ
る。FIG. 3 is a diagram showing the relationship between cold working rate and creep deformation.
【図４】冷間加工率と引張強度の関係を示す図である。FIG. 4 is a diagram showing the relationship between cold working rate and tensile strength.
Claims (1)
て溶体化処理を行った後、１％〜５％未満の冷間加工を
行い、次いで、時効処理を行うことを特徴とするジルコ
ニウム合金の製造方法。[Claim 1] Production of a zirconium alloy characterized by subjecting an (α+β) type zirconium alloy to solution treatment, followed by cold working of 1% to less than 5%, and then aging treatment. Method.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP14647391A JPH04329855A (en) | 1991-04-30 | 1991-04-30 | Production of zirconium alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP14647391A JPH04329855A (en) | 1991-04-30 | 1991-04-30 | Production of zirconium alloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH04329855A true JPH04329855A (en) | 1992-11-18 |
Family
ID=15408438
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP14647391A Withdrawn JPH04329855A (en) | 1991-04-30 | 1991-04-30 | Production of zirconium alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH04329855A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100737700B1 (en) * | 2004-10-28 | 2007-07-10 | 한국원자력연구원 | Tubes of Zr based alloys and their Manufacturing Method |
-
1991
- 1991-04-30 JP JP14647391A patent/JPH04329855A/en not_active Withdrawn
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100737700B1 (en) * | 2004-10-28 | 2007-07-10 | 한국원자력연구원 | Tubes of Zr based alloys and their Manufacturing Method |
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