JPS60100655A - Production of high cr-containing ni-base alloy member having excellent resistance to stress corrosion cracking - Google Patents
Production of high cr-containing ni-base alloy member having excellent resistance to stress corrosion crackingInfo
- Publication number
- JPS60100655A JPS60100655A JP58207248A JP20724883A JPS60100655A JP S60100655 A JPS60100655 A JP S60100655A JP 58207248 A JP58207248 A JP 58207248A JP 20724883 A JP20724883 A JP 20724883A JP S60100655 A JPS60100655 A JP S60100655A
- Authority
- JP
- Japan
- Prior art keywords
- hot working
- working
- corrosion cracking
- stress corrosion
- conditions
- 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.)
- Granted
Links
- 238000005260 corrosion Methods 0.000 title claims abstract description 26
- 230000007797 corrosion Effects 0.000 title claims abstract description 26
- 239000000956 alloy Substances 0.000 title claims abstract description 21
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 21
- 238000005336 cracking Methods 0.000 title claims abstract description 18
- 238000004519 manufacturing process Methods 0.000 title claims description 10
- 238000010438 heat treatment Methods 0.000 claims abstract description 36
- 238000001953 recrystallisation Methods 0.000 claims abstract description 6
- 238000005482 strain hardening Methods 0.000 claims abstract description 4
- 238000000034 method Methods 0.000 claims description 10
- 238000012545 processing Methods 0.000 claims description 10
- 238000005242 forging Methods 0.000 claims description 3
- 239000002244 precipitate Substances 0.000 abstract description 3
- 239000007787 solid Substances 0.000 abstract 1
- 150000001247 metal acetylides Chemical class 0.000 description 13
- 238000001556 precipitation Methods 0.000 description 8
- 238000012360 testing method Methods 0.000 description 7
- 230000003245 working effect Effects 0.000 description 5
- 238000012733 comparative method Methods 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- 239000006104 solid solution Substances 0.000 description 3
- QAOWNCQODCNURD-UHFFFAOYSA-N Sulfuric acid Chemical compound OS(O)(=O)=O QAOWNCQODCNURD-UHFFFAOYSA-N 0.000 description 2
- 238000005452 bending Methods 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 238000005098 hot rolling Methods 0.000 description 2
- 239000012535 impurity Substances 0.000 description 2
- 238000003754 machining Methods 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 239000000243 solution Substances 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- 238000000137 annealing Methods 0.000 description 1
- 229910052796 boron Inorganic materials 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 230000002950 deficient Effects 0.000 description 1
- 238000007872 degassing Methods 0.000 description 1
- 230000001814 effect on stress Effects 0.000 description 1
- 238000007654 immersion Methods 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 150000002500 ions Chemical class 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- RUTXIHLAWFEWGM-UHFFFAOYSA-H iron(3+) sulfate Chemical compound [Fe+3].[Fe+3].[O-]S([O-])(=O)=O.[O-]S([O-])(=O)=O.[O-]S([O-])(=O)=O RUTXIHLAWFEWGM-UHFFFAOYSA-H 0.000 description 1
- 229910000360 iron(III) sulfate Inorganic materials 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 231100000989 no adverse effect Toxicity 0.000 description 1
- 230000001376 precipitating effect Effects 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 239000000758 substrate Substances 0.000 description 1
- 229910052715 tantalum Inorganic materials 0.000 description 1
- 238000011282 treatment Methods 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Landscapes
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Nonferrous Metals Or Alloys (AREA)
Abstract
Description
【発明の詳細な説明】
この発明は、結晶粒界に析出して応力腐食割れ発生の原
因となる人／Ｉ２ａ Ｃａ型炭化物の析出を抑制し、一
方熱間加工時には積極的に素地中にＭ、Ｃ，型炭化物を
均一微細に析出させるととによって耐応力腐食割ね性の
すぐれた高Ｃｒ含有Ｎｉ基合金部材を製造する方法に関
するものである。DETAILED DESCRIPTION OF THE INVENTION The present invention suppresses the precipitation of Ca/I2a type carbides that precipitate at grain boundaries and cause stress corrosion cracking, while actively inhibiting the formation of M in the substrate during hot working. The present invention relates to a method for producing a high Cr-containing Ni-based alloy member with excellent stress corrosion cracking resistance by uniformly and finely precipitating , C, type carbides.
従来、例えば高温高圧にさらされる軽水型原子炉の構造
部材などの製造には、耐食性向上成分としてのＣｒ：１
３〜３３％、および加工性向上成分としてのＦｅ ：
５〜１５％を含有し、さらに必要に応じて脱酸成分およ
び強度向上成分としてｓｉ 、 Ｍｎ 、 Ａｌ ＋Ｔ
ｉ 、 Ｚｒ 、 Ｂ 、 Ｎｂ 、 Ｔａ 、 Ｗ
、およびＶなどのうちの１種または２種以上をそれぞれ
０．１〜１％含有し、かつ耐応力腐食割れ性を低下させ
る不可避不純物としてのＣ含有量を０．１％以下とし、
残りがＮｉとその他の不可避不純物からなる組成（以上
重量％）を有するＮｉ基合金が使用されている。Conventionally, for example, in the production of structural members of light water nuclear reactors exposed to high temperature and high pressure, Cr:1 was used as a corrosion resistance improving component.
3 to 33%, and Fe as a processability improving component:
5 to 15%, and further contains si, Mn, Al + T as a deoxidizing component and a strength improving component as necessary.
i, Zr, B, Nb, Ta, W
, V, etc., each containing 0.1 to 1% of one or more of V, and the C content as an unavoidable impurity that reduces stress corrosion cracking resistance is 0.1% or less,
A Ni-based alloy having a composition (weight %) of Ni and other unavoidable impurities is used.
また、これらの高Ｃｒ含有Ｎｉ基合金部材は、通常、イ
ンゴットを、１１５０〜１２５０℃の温度で分塊鍛造し
た後、加熱温度： １１００〜１２００℃、加工終了温
度二８００℃以上の条件で熱間加工し、必要に応じて冷
間加工を施し、最終的に歪取シ、再結晶化、あるいは溶
体化のだめの熱処理を施すことによって製造されている
。In addition, these high Cr-containing Ni-based alloy members are usually produced by blooming an ingot at a temperature of 1,150 to 1,250°C, and then heat treatment at a heating temperature of 1,100 to 1,200°C and a finishing temperature of 2,800°C or higher. It is manufactured by subjecting it to temporary processing, cold working if necessary, and finally heat treatment for strain relief, recrystallization, or solution treatment.
しかし、このような高Ｃｒ含有Ｎｉ基合金部材の製造法
においては、熱間加工あるいは熱処理時などの冷却過程
でＭ２Ｓ Ｃｅ型炭化物が結晶粒界に連続して析出する
のを避けることができず、この結果Ｃｒ欠乏層が形成し
、このＣｒ欠乏層は応力腐食割れの原因となることから
、例えば特公昭５８−１７８２３号公報に記載されるよ
うな特別な条件での熱処理を施してＣｒ欠乏層の消失を
はかつているが、これらの熱処理はいずれも長時間を要
し、かつ制御が面倒でちるなどの問題点がある。However, in this method of manufacturing high Cr-containing Ni-based alloy members, it is impossible to avoid continuous precipitation of M2S Ce type carbides at grain boundaries during hot working or cooling during heat treatment. As a result, a Cr-depleted layer is formed, and since this Cr-depleted layer causes stress corrosion cracking, a heat treatment under special conditions as described in Japanese Patent Publication No. 58-17823 is performed to eliminate the Cr-depleted layer. Although the layer is on the verge of disappearing, all of these heat treatments require a long time and have problems such as being cumbersome and cumbersome to control.
そこで、本発明者等は、上述のような観点から、特別な
条件での熱処理を必要とすることなく、耐応力腐食割れ
性のすぐれた高Ｃｒ含有Ｎｉ基合金部材を製造すべく研
究を行なった結果、前記部材の熱間加工に際して、初回
の熱間加工における加熱温度を１０８０℃以上として完
全固溶体とし、かつ加工終了温度を７００〜８００℃と
してＭ２Ｏ，型炭化物が粒界および粒内を問わず、素地
中に積極的に均一微細に分散析出した組織を得るように
し、引続いての２回以降の熱間加工を、前記初回熱間加
工時に析出した微細なＭ２Ｏ，型炭化物を固溶させない
ために、加熱温度を９００〜１０５０’Ｃとし、加工終
了温度を初回熱間加工の場合と同じ＜ ７００〜８００
°Ｃとした条件で行ない、さらに最終的に施される再結
晶化あるいは歪取りのだめの熱処理を、７５０〜１０５
０℃の温度で行なって、上記の熱間加工時に形成された
組織、すなわち微細なＭ、Ｃ，型炭化物が均一に分散析
出した組織が損表われないようにすると、この結果得ら
れた高Ｃｒ含有Ｎｉ基合金部材は、 Ｃｒ欠乏層発生の
原因となるＭ２Ｓ ０ａ型炭化物の連続した結晶粒界析
出がないことから、すぐれた耐応力腐食割れ性を具備す
るという知見を得たのである。Therefore, from the above-mentioned viewpoint, the present inventors conducted research to produce a high Cr-containing Ni-based alloy member with excellent stress corrosion cracking resistance without requiring heat treatment under special conditions. As a result, when hot working the above-mentioned member, the heating temperature in the first hot working was set to 1080°C or higher to form a complete solid solution, and the processing end temperature was set to 700 to 800°C, so that M2O and type carbides were formed at the grain boundaries and inside the grains. First, actively obtain a structure that is uniformly and finely dispersed and precipitated in the base material, and in the subsequent hot workings, the fine M2O and type carbides precipitated during the first hot working are dissolved in solid solution. In order to prevent this, the heating temperature is set to 900-1050'C, and the finishing temperature is the same as the initial hot working <700-800'C.
°C, and the final heat treatment for recrystallization or strain relief is carried out at 750 to 105 °C.
If the process is carried out at a temperature of 0°C so that the structure formed during the above hot working, that is, the structure in which fine M, C, and type carbides are uniformly dispersed and precipitated, is not damaged, the resulting high It was found that Cr-containing Ni-based alloy members have excellent stress corrosion cracking resistance because there is no continuous grain boundary precipitation of M2S 0a type carbide, which causes the generation of Cr-depleted layers.
この発明は、上記知見にもとづいてなされたものであっ
て、高Ｃｒ含有Ｎｉ基合金部材の製造法において、初回
の熱間加工条件を、加熱温度： １０８０℃以上、加工
終了温度ニア００〜８００℃とし、２回以降の熱間加工
条件を、加熱温度：９００〜１０５００Ｇ、加工終了温
度＝７００〜８００℃とした条件で熱間加工を行ない、
さらに前記の熱間加工、あるいは前記の熱間加工および
通常の条件での冷間加工後の部材に対して、７５０〜１
０５０℃の温度で歪取シあるいは再結晶化のための熱処
理を施すことによって、耐応力腐食割れ性のすぐ九た高
Ｃｒ含有Ｎｉ基合金部材を製造する方法に特徴を有する
ものである。This invention has been made based on the above knowledge, and in a method for manufacturing a high Cr-containing Ni-based alloy member, the initial hot working conditions are heating temperature: 1080°C or higher, working end temperature near 00 to 800°C. ℃, and the hot working conditions from the second time onwards were heating temperature: 900 to 10500G, processing end temperature = 700 to 800℃,
Furthermore, 750 to 1
The present invention is characterized by a method for producing a highly Cr-containing Ni-based alloy member with excellent stress corrosion cracking resistance by subjecting it to heat treatment for strain relief or recrystallization at a temperature of 0.050°C.
つぎに、この発明の高Ｃｒ含有Ｎｉ基合金部材の製造法
において、熱間加工条件および熱処理条件を上記の通シ
に限定した理由を説明する。Next, the reason why the hot working conditions and heat treatment conditions are limited to the above-mentioned conditions in the method of manufacturing a high Cr-containing Ni-based alloy member of the present invention will be explained.
（ａ） 初回熱間加工め加熱温度
その加熱温度がＩ ０８０℃未満では、前工程の分塊鍛
造あるいは熱間鍛造で析出したＭ２Ｓ Ｃ６型炭化物を
完全に固溶させることができないので、１０８０℃以上
の温度に加熱しなければならないが、 １２００℃を越
えると結晶粒が粗大化するようになるので、１２００℃
を越えて加熱することは望ましくない。(a) Heating temperature for initial hot working If the heating temperature is less than 1080°C, it is impossible to completely dissolve the M2S C6 type carbide precipitated in the previous step of blooming or hot forging. It is necessary to heat the product to a temperature higher than 1200°C, but if it exceeds 1200°C, the crystal grains will become coarse.
It is undesirable to heat the product beyond this point.
（ｂ） 初回熱間加工の加工終了温度
初回の熱間加工に際しては、耐応力腐食割れ住方化の原
因となるＭ２Ｓ ０６型炭化物を析出させることなく、
耐応力腐食割れ性に何らの悪影響も及ぼさない微細なＭ
ＴＣ１ｌ型炭化物全炭化物せるようにするものであるた
め、その加工終了温度をＭ７Ｃ３型炭化物の析出速度が
最も速い温度域である７００〜８００℃とすることによ
ってＭ、Ｃ３型炭化物を積極的に析出させるようにする
のである。したがって、加工終了温度が８００℃を越え
た高温であるとＭ７Ｃ３型炭化物の析出が緩慢となって
望ましくなく、一方その加工終了温度が７００℃未満に
なるとＭ２Ｓ Ｃ６型炭化物が析出するようになるので
あって、かかる理由から、その加工終了温度を７００〜
８００℃と定めた。(b) Processing end temperature of first hot working During the first hot working, M2S06 type carbide, which causes stress corrosion cracking, is not precipitated.
Fine M that has no adverse effect on stress corrosion cracking resistance
Since all of the TC1l type carbides are to be formed, M and C3 type carbides are actively precipitated by setting the processing end temperature to 700 to 800°C, which is the temperature range in which the precipitation rate of M7C3 type carbides is the fastest. Let them do it. Therefore, if the machining end temperature is high enough to exceed 800°C, the precipitation of M7C3 type carbide will become slow, which is undesirable, whereas if the machining end temperature is less than 700°C, M2S C6 type carbide will precipitate. For this reason, the processing end temperature is set at 700~
The temperature was set at 800°C.
（ｃ）２回以降の熱間加工における加熱温度その加熱温
度が１０５０℃を越えると、初回熱間加工で折角析出さ
せた微細なＭ７Ｃ３型炭化物が再び固溶するようになシ
、一方、その加熱温度が、９０００Ｃ未満になると熱間
加工を工業的に実施することが困難になることから、そ
の加熱温度を９００〜１０５０℃と定めた。(c) Heating temperature in second and subsequent hot workings If the heating temperature exceeds 1050°C, the fine M7C3 type carbides that were painstakingly precipitated in the first hot working will become solid solution again. If the heating temperature is less than 9000C, it will be difficult to carry out hot working industrially, so the heating temperature was set at 900 to 1050C.
（ｄ）２回以降の熱間加工における加工終了温度２回以
降の熱間加工における加工終了温度も初回熱間加工にお
けると同じ理由によって定めたのであって、Ｍ、Ｃ３型
炭化物の析出速度の速い７００〜８００℃の温度域で熱
間加工を終了するようにしたのでちる。(d) Processing end temperature for the second and subsequent hot workings The processing end temperature for the second and subsequent hot workings was determined for the same reason as for the first hot working, and the precipitation rate of M and C3 type carbides. Hot working is finished in a fast temperature range of 700 to 800°C.
なお、Ｍ７Ｃ３型炭化物の析出は、熱間加工におけるＪ
加熱当９の力Ｐ工率が２０％以上になると一段と促進さ
れるようになる。また、冷間加工に際して、中間焼鈍を
行なう必要がある場合、その加熱温度が上記の２回以降
の熱間加工における加熱温度と同じ９００〜１０５０℃
となるとどけ勿論である。Note that the precipitation of M7C3 type carbides is caused by J during hot working.
When the power P power rate of the heating element 9 becomes 20% or more, it will be further accelerated. In addition, if it is necessary to perform intermediate annealing during cold working, the heating temperature should be 900 to 1050°C, which is the same as the heating temperature in the second and subsequent hot workings mentioned above.
Of course, that's the case.
つぎに、この発明の高Ｃｒ含有Ｎｌ基合金部材の製造法
を実施例により説明する。Next, the method for manufacturing a high Cr-containing Nl-based alloy member of the present invention will be explained using examples.
実施例
通常の溶解法により、第１表に示される成分組成をもっ
た高Ｃｒ含有Ｎｉ基合金を溶製し、直径：３００ ｍＦ
Ａφ×長さ： １０００ｍ＋ｉの寸法をもったインゴッ
トに鋳造した後、いずれも１２００℃に加熱して分塊鍛
造を施し、それぞれ第１表に示される厚さのスラブとし
、ついで同じく第１表に示される条件にて初回熱間圧延
を施し、引続いて同じく第１表に示される条件にて２回
以降の熱間ｆｆ延を行ない、最終的に同じく第１表に示
される条件にて再結晶化のだめの熱処理（熱処理後の冷
却はいずれも急冷）を施すことによって本発明法１〜５
および比較法１〜７をそれぞれ実施した。なお、比較法
１〜７は、いずれも熱間加工条件および熱処理条件のう
ちのいずれかの条件（第１表に※印を付したもの）がこ
の発明の範囲から外わた条件で実施したものである。Example A high Cr-containing Ni-based alloy having the composition shown in Table 1 was melted using a conventional melting method, and a diameter: 300 mF was prepared.
Aφ x length: After casting into ingots with dimensions of 1000 m + i, they were heated to 1200°C and subjected to blooming forging to form slabs with the thickness shown in Table 1. The first hot rolling was carried out under the conditions shown in Table 1, followed by the second hot FF rolling under the conditions shown in Table 1, and the final hot rolling was carried out again under the conditions shown in Table 1. Methods 1 to 5 of the present invention can be obtained by heat treatment (cooling after heat treatment is rapid) to prevent crystallization.
and Comparative Methods 1 to 7 were carried out, respectively. In addition, Comparative Methods 1 to 7 were all conducted under conditions in which any of the hot working conditions and heat treatment conditions (those marked with * in Table 1) were outside the scope of this invention. It is.
ついで、上記本発明法１〜５および比較法１〜７によっ
て得られた板材について、応力腐食割れ試験および粒界
腐食試験を行なった。応力腐食割れ試験は、幅”、１５
ｍｍＸ長さ：１００龍×厚さ＝２ｍｍの板材を２枚重ね
てＵ字型に曲げた、いわゆる２重Ｕ字曲げ試験片を用い
、この試験片を、５００ｐｐｍのＣ／？イオンを含有し
、かつ脱気しない３００’Ｃの高温水中に１０００時間
浸漬の条件で行ない、試験後、最大応力腐食割れ深さを
測定Ｉ７た。また、粒界腐食試験は、ＡＳＴＭ−０２８
にもとづき、硫酸・硫酸第２鉄溶液中における粒界腐食
速度を測定することにより行なった。これらの測定結果
を第１表に合せて示した。Next, a stress corrosion cracking test and an intergranular corrosion test were conducted on the plate materials obtained by the above-mentioned methods 1 to 5 of the present invention and comparative methods 1 to 7. Stress corrosion cracking test
mm x length: 100 mm x thickness = 2 mm A so-called double U-shaped bending test piece was used, which was made by stacking two plates and bending them into a U-shape. The test was carried out under conditions of 1000 hours of immersion in 300'C high temperature water containing ions and without degassing, and after the test, the maximum stress corrosion cracking depth was measured I7. In addition, the intergranular corrosion test is performed using ASTM-028
Based on this, the intergranular corrosion rate was measured in a sulfuric acid/ferric sulfate solution. These measurement results are also shown in Table 1.
第１表に示される結果から、本発明法１〜５によって製
造された高Ｃｒ含有Ｎｉ基合金部材においては、結晶粒
界にＭ２ｊ Ｃｅ型炭化物の析出がなく、シたがってＣ
ｒ欠乏層の形成がないことから、すぐれた耐応力腐食割
れ性を示し、かつ粒界腐食速度も遅く、すぐれた耐粒界
腐食性を示すことが明らかである。これに対して、比較
法１〜７によって製造された高Ｃｒ含有Ｎｉ基合金板材
に見られるように、熱間加工条件および熱処理条件のう
ちのいずれかの条件でもこの発明の範囲から外ねると、
耐応力腐食割れ性および耐粒界腐食性のすぐれた高Ｃｒ
含有Ｎｉ基合金部材を得ることができないことが明らか
である。From the results shown in Table 1, in the high Cr-containing Ni-based alloy members manufactured by methods 1 to 5 of the present invention, there is no precipitation of M2j Ce-type carbides at grain boundaries, and therefore C
Since there is no formation of an r-deficient layer, it is clear that the material exhibits excellent stress corrosion cracking resistance, and the intergranular corrosion rate is also slow, indicating excellent intergranular corrosion resistance. On the other hand, as seen in the high Cr-containing Ni-based alloy sheet materials manufactured by Comparative Methods 1 to 7, any of the hot working conditions and heat treatment conditions are outside the scope of the present invention. ,
High Cr with excellent stress corrosion cracking resistance and intergranular corrosion resistance
It is clear that it is not possible to obtain a containing Ni-based alloy member.
上述のように、この発明の方法によれば、特別な熱処理
条件を必要とすることなく、単に熱間加工における加熱
温度および加工終了温度、並びに出願人 三菱金属株式
会社
代理人 富 １）和 夫 外１名As described above, according to the method of the present invention, there is no need for special heat treatment conditions, and the heating temperature and processing end temperature in hot working are simply controlled, and the applicant Mitsubishi Metals Co., Ltd. Agent Tomi 1) Kazuo 1 other person
Claims (1)
後の初回の熱間加工条件を、加熱温度： １０８０℃以
上、加工終了温度ニア００〜８００℃とし、２回以降の
熱間加工条件を、加熱温度＝９００〜１０５０℃、加工
終了温度ニア００〜８００℃とした条件で熱間加工を行
ない、さらに前記の熱間加工、あるいは前記の熱間加工
および通常の条件での冷間加工後の部材に対して、７５
０〜１０５０℃の温度で歪取シおよび再結晶化のだめの
熱処理を施すことを特徴とする耐応力腐食割ね性のすぐ
れた高Ｃｒ含有Ｎｉ基合金部材の製造法。In the method for manufacturing a high Cr-containing Ni-based alloy member, the first hot working conditions after blooming forging are heating temperature: 1080°C or higher, working end temperature near 00 to 800°C, and the second and subsequent hot working conditions. is hot worked under the conditions of heating temperature = 900 to 1050°C and processing end temperature near 00 to 800°C, and further hot working as described above, or hot working as described above and cold working under normal conditions. For the latter part, 75
A method for manufacturing a high Cr-containing Ni-based alloy member having excellent stress corrosion cracking resistance, which comprises performing heat treatment for strain relief and recrystallization at a temperature of 0 to 1050°C.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP58207248A JPS60100655A (en) | 1983-11-04 | 1983-11-04 | Production of high cr-containing ni-base alloy member having excellent resistance to stress corrosion cracking |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP58207248A JPS60100655A (en) | 1983-11-04 | 1983-11-04 | Production of high cr-containing ni-base alloy member having excellent resistance to stress corrosion cracking |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS60100655A true JPS60100655A (en) | 1985-06-04 |
| JPS6157390B2 JPS6157390B2 (en) | 1986-12-06 |
Family
ID=16536661
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP58207248A Granted JPS60100655A (en) | 1983-11-04 | 1983-11-04 | Production of high cr-containing ni-base alloy member having excellent resistance to stress corrosion cracking |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS60100655A (en) |
Cited By (18)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5019179A (en) * | 1989-03-20 | 1991-05-28 | Mitsubishi Metal Corporation | Method for plastic-working ingots of heat-resistant alloy containing boron |
| JP2011162819A (en) * | 2010-02-05 | 2011-08-25 | Mitsubishi Materials Corp | Ni-BASED ALLOY, AND METHOD FOR PRODUCING Ni-BASED ALLOY |
| WO2012166295A3 (en) * | 2011-06-01 | 2013-01-24 | Ati Properties, Inc. | Thermo-mechanical processing of nickel-base alloys |
| US8834653B2 (en) | 2010-07-28 | 2014-09-16 | Ati Properties, Inc. | Hot stretch straightening of high strength age hardened metallic form and straightened age hardened metallic form |
| US9050647B2 (en) | 2013-03-15 | 2015-06-09 | Ati Properties, Inc. | Split-pass open-die forging for hard-to-forge, strain-path sensitive titanium-base and nickel-base alloys |
| US9192981B2 (en) | 2013-03-11 | 2015-11-24 | Ati Properties, Inc. | Thermomechanical processing of high strength non-magnetic corrosion resistant material |
| US9206497B2 (en) | 2010-09-15 | 2015-12-08 | Ati Properties, Inc. | Methods for processing titanium alloys |
| US9255316B2 (en) | 2010-07-19 | 2016-02-09 | Ati Properties, Inc. | Processing of α+β titanium alloys |
| US9523137B2 (en) | 2004-05-21 | 2016-12-20 | Ati Properties Llc | Metastable β-titanium alloys and methods of processing the same by direct aging |
| US9777361B2 (en) | 2013-03-15 | 2017-10-03 | Ati Properties Llc | Thermomechanical processing of alpha-beta titanium alloys |
| US9796005B2 (en) | 2003-05-09 | 2017-10-24 | Ati Properties Llc | Processing of titanium-aluminum-vanadium alloys and products made thereby |
| US9869003B2 (en) | 2013-02-26 | 2018-01-16 | Ati Properties Llc | Methods for processing alloys |
| US10053758B2 (en) | 2010-01-22 | 2018-08-21 | Ati Properties Llc | Production of high strength titanium |
| US10094003B2 (en) | 2015-01-12 | 2018-10-09 | Ati Properties Llc | Titanium alloy |
| US10435775B2 (en) | 2010-09-15 | 2019-10-08 | Ati Properties Llc | Processing routes for titanium and titanium alloys |
| US10502252B2 (en) | 2015-11-23 | 2019-12-10 | Ati Properties Llc | Processing of alpha-beta titanium alloys |
| US10513755B2 (en) | 2010-09-23 | 2019-12-24 | Ati Properties Llc | High strength alpha/beta titanium alloy fasteners and fastener stock |
| US11111552B2 (en) | 2013-11-12 | 2021-09-07 | Ati Properties Llc | Methods for processing metal alloys |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5864364A (en) * | 1981-10-14 | 1983-04-16 | Sumitomo Metal Ind Ltd | Manufacture of ni-cr alloy with superior corrosion resistance |
| JPS5867854A (en) * | 1981-10-16 | 1983-04-22 | Sumitomo Metal Ind Ltd | Preparation of nickel base high chromium alloy excellent in stress, corrosion cracking resistance |
| JPS58153763A (en) * | 1982-03-05 | 1983-09-12 | Sumitomo Metal Ind Ltd | Preparation of nickel-chromium alloy |
-
1983
- 1983-11-04 JP JP58207248A patent/JPS60100655A/en active Granted
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5864364A (en) * | 1981-10-14 | 1983-04-16 | Sumitomo Metal Ind Ltd | Manufacture of ni-cr alloy with superior corrosion resistance |
| JPS5867854A (en) * | 1981-10-16 | 1983-04-22 | Sumitomo Metal Ind Ltd | Preparation of nickel base high chromium alloy excellent in stress, corrosion cracking resistance |
| JPS58153763A (en) * | 1982-03-05 | 1983-09-12 | Sumitomo Metal Ind Ltd | Preparation of nickel-chromium alloy |
Cited By (34)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5019179A (en) * | 1989-03-20 | 1991-05-28 | Mitsubishi Metal Corporation | Method for plastic-working ingots of heat-resistant alloy containing boron |
| US9796005B2 (en) | 2003-05-09 | 2017-10-24 | Ati Properties Llc | Processing of titanium-aluminum-vanadium alloys and products made thereby |
| US10422027B2 (en) | 2004-05-21 | 2019-09-24 | Ati Properties Llc | Metastable beta-titanium alloys and methods of processing the same by direct aging |
| US9523137B2 (en) | 2004-05-21 | 2016-12-20 | Ati Properties Llc | Metastable β-titanium alloys and methods of processing the same by direct aging |
| US10053758B2 (en) | 2010-01-22 | 2018-08-21 | Ati Properties Llc | Production of high strength titanium |
| JP2011162819A (en) * | 2010-02-05 | 2011-08-25 | Mitsubishi Materials Corp | Ni-BASED ALLOY, AND METHOD FOR PRODUCING Ni-BASED ALLOY |
| US9255316B2 (en) | 2010-07-19 | 2016-02-09 | Ati Properties, Inc. | Processing of α+β titanium alloys |
| US9765420B2 (en) | 2010-07-19 | 2017-09-19 | Ati Properties Llc | Processing of α/β titanium alloys |
| US10144999B2 (en) | 2010-07-19 | 2018-12-04 | Ati Properties Llc | Processing of alpha/beta titanium alloys |
| US8834653B2 (en) | 2010-07-28 | 2014-09-16 | Ati Properties, Inc. | Hot stretch straightening of high strength age hardened metallic form and straightened age hardened metallic form |
| US10435775B2 (en) | 2010-09-15 | 2019-10-08 | Ati Properties Llc | Processing routes for titanium and titanium alloys |
| US9624567B2 (en) | 2010-09-15 | 2017-04-18 | Ati Properties Llc | Methods for processing titanium alloys |
| US9206497B2 (en) | 2010-09-15 | 2015-12-08 | Ati Properties, Inc. | Methods for processing titanium alloys |
| US10513755B2 (en) | 2010-09-23 | 2019-12-24 | Ati Properties Llc | High strength alpha/beta titanium alloy fasteners and fastener stock |
| CN103597105A (en) * | 2011-06-01 | 2014-02-19 | Ati资产公司 | Thermo-mechanical processing of nickel-base alloys |
| JP2014520206A (en) * | 2011-06-01 | 2014-08-21 | エイティーアイ・プロパティーズ・インコーポレーテッド | Thermomechanical processing of nickel-based alloys |
| CN107254606A (en) * | 2011-06-01 | 2017-10-17 | 冶联科技地产有限责任公司 | Nickel-based alloy, article comprising the alloy and thermomechanical processing of the alloy |
| US10287655B2 (en) | 2011-06-01 | 2019-05-14 | Ati Properties Llc | Nickel-base alloy and articles |
| WO2012166295A3 (en) * | 2011-06-01 | 2013-01-24 | Ati Properties, Inc. | Thermo-mechanical processing of nickel-base alloys |
| US9616480B2 (en) | 2011-06-01 | 2017-04-11 | Ati Properties Llc | Thermo-mechanical processing of nickel-base alloys |
| US9869003B2 (en) | 2013-02-26 | 2018-01-16 | Ati Properties Llc | Methods for processing alloys |
| US10570469B2 (en) | 2013-02-26 | 2020-02-25 | Ati Properties Llc | Methods for processing alloys |
| US10337093B2 (en) | 2013-03-11 | 2019-07-02 | Ati Properties Llc | Non-magnetic alloy forgings |
| US9192981B2 (en) | 2013-03-11 | 2015-11-24 | Ati Properties, Inc. | Thermomechanical processing of high strength non-magnetic corrosion resistant material |
| US10370751B2 (en) | 2013-03-15 | 2019-08-06 | Ati Properties Llc | Thermomechanical processing of alpha-beta titanium alloys |
| US9050647B2 (en) | 2013-03-15 | 2015-06-09 | Ati Properties, Inc. | Split-pass open-die forging for hard-to-forge, strain-path sensitive titanium-base and nickel-base alloys |
| US9777361B2 (en) | 2013-03-15 | 2017-10-03 | Ati Properties Llc | Thermomechanical processing of alpha-beta titanium alloys |
| US11111552B2 (en) | 2013-11-12 | 2021-09-07 | Ati Properties Llc | Methods for processing metal alloys |
| US11851734B2 (en) | 2015-01-12 | 2023-12-26 | Ati Properties Llc | Titanium alloy |
| US10619226B2 (en) | 2015-01-12 | 2020-04-14 | Ati Properties Llc | Titanium alloy |
| US10808298B2 (en) | 2015-01-12 | 2020-10-20 | Ati Properties Llc | Titanium alloy |
| US11319616B2 (en) | 2015-01-12 | 2022-05-03 | Ati Properties Llc | Titanium alloy |
| US10094003B2 (en) | 2015-01-12 | 2018-10-09 | Ati Properties Llc | Titanium alloy |
| US10502252B2 (en) | 2015-11-23 | 2019-12-10 | Ati Properties Llc | Processing of alpha-beta titanium alloys |
Also Published As
| Publication number | Publication date |
|---|---|
| JPS6157390B2 (en) | 1986-12-06 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JPS60100655A (en) | Production of high cr-containing ni-base alloy member having excellent resistance to stress corrosion cracking | |
| KR100260111B1 (en) | Thermomechanical processing of metallic materials | |
| GB2160894A (en) | Processing aluminium alloy sheet for good formability | |
| JP2002146497A (en) | METHOD FOR MANUFACTURING Ni-BASED ALLOY | |
| KR101630403B1 (en) | Manufacture method of nuclear fuel component made of zirconium applied multi-stage cold rolling | |
| JPS5850299B2 (en) | Manufacturing method for precipitation-strengthened high-strength cold-rolled steel sheets | |
| US2799602A (en) | Process for producing stainless steel | |
| JPS60197817A (en) | Manufacture of austenitic stainless steel material having high yield strength and superior corrosion resistance | |
| JPS5953347B2 (en) | Manufacturing method of aircraft stringer material | |
| JPS6389649A (en) | Manufacture of al-mg-zn alloy material having superior formability | |
| JP2738130B2 (en) | High strength Cu alloy continuous casting mold material having high cooling capacity and method for producing the same | |
| US4435231A (en) | Cold worked ferritic alloys and components | |
| JP4414588B2 (en) | Ni-based alloy with excellent surface quality and method for producing the same | |
| JPH0461057B2 (en) | ||
| JPS604884B2 (en) | Manufacturing method of super strong Kamalage steel | |
| JPS6123862B2 (en) | ||
| KR20150105343A (en) | Treatment process for a zirconium alloy, zirconium alloy resulting from this process and parts of nuclear reactors made of this alloy | |
| JPH08239739A (en) | Heat tratment for ni-base alloy excellent in corrosion resistance | |
| JPS6324062B2 (en) | ||
| JPH03130351A (en) | Production of titanium and titanium alloy having fine and equiaxial structure | |
| JPH05202444A (en) | Steel plate excellent in toughness at low temperature and its production | |
| JPH11335803A (en) | Production of near beta type titanium alloy coil | |
| JPS5873754A (en) | Manufacture of ni-cr alloy with superior corrosion resistance and strength | |
| JPS6240336A (en) | Ni-fe-cr alloy sheet material superior in cold formability and its manufacture | |
| JPS61159563A (en) | Production of industrial pure titanium forging stock excellent in mechanical strength |