JPS6130655A - Stainless cast steel having superior resistance to cavitation erosion and corrosion by seawater - Google Patents
Stainless cast steel having superior resistance to cavitation erosion and corrosion by seawaterInfo
- Publication number
- JPS6130655A JPS6130655A JP14940484A JP14940484A JPS6130655A JP S6130655 A JPS6130655 A JP S6130655A JP 14940484 A JP14940484 A JP 14940484A JP 14940484 A JP14940484 A JP 14940484A JP S6130655 A JPS6130655 A JP S6130655A
- Authority
- JP
- Japan
- Prior art keywords
- phase
- cast steel
- seawater
- erosion
- cavitation
- 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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Abstract
Description
【発明の詳細な説明】
〔発明の利用分野〕
本発明は、耐キャビテーション・エロージヨン性と耐海
水腐食性に優れ、特に海水ポンプのインペラに好適なス
テンレス鋳鋼に関する。DETAILED DESCRIPTION OF THE INVENTION [Field of Application of the Invention] The present invention relates to a stainless steel cast steel that has excellent cavitation/erosion resistance and seawater corrosion resistance and is particularly suitable for impellers of seawater pumps.
最近、海水ポンプや海水揚水発電用水車（以下海水ポン
プと記す）が高速化、小型化、高揚程化されるに伴いイ
ンペラ（以下水車も含む）のキャ９゜
ビテーション・エロション損傷が目立って発生しはじめ
、ポンプ寿命を左右する状態にまで致った。Recently, as seawater pumps and water turbines for seawater pumped storage power generation (hereinafter referred to as seawater pumps) have become faster, smaller, and have higher head, cavitation and erosion damage to impellers (hereinafter also referred to as water turbines) has become noticeable. This has started to occur and has reached the point where it affects the life of the pump.
一方、従来のポンプインペラは１３ Ｃｒ％Ｎｉ含有−
１３Ｃｒおよび１８ Ｃｒ −８Ｎ ｉ系ステンレス鋼
が用いられて来たが、上述のように耐キャビテーション
・エロージヨン性および耐海水腐食性が不十分である。On the other hand, conventional pump impellers contain 13 Cr%Ni.
13Cr and 18Cr-8Ni stainless steels have been used, but as mentioned above, they have insufficient cavitation/erosion resistance and seawater corrosion resistance.
これらを満すため、オーステナイト相あるいはイプシロ
ン相からなるステンレス鋼（例えば特開昭５７−１５２
４４７号）が提案されているが、耐キャビテーション性
や耐海水腐食性が不十分であり、鋳造性、溶接性につい
ても配慮されていない。In order to satisfy these requirements, stainless steel consisting of austenite phase or epsilon phase (for example, JP-A-57-152
No. 447) has been proposed, but its cavitation resistance and seawater corrosion resistance are insufficient, and castability and weldability are not considered.
本発明は上記に鑑みてなしたもので、耐キャビテーショ
ン・エロージヨン性と耐海水腐食性に優れるとともに鋳
造性・溶接性も良好なステンレス鋳鋼を提供することを
目的とする。The present invention was made in view of the above, and an object of the present invention is to provide a stainless steel cast steel that is excellent in cavitation/erosion resistance and seawater corrosion resistance, and also has good castability and weldability.
本発明（以下第１の発明という）のステンレス鋳銅はＣ
； ０．０５〜０．１％、Ｓｉ；０．１〜１．５％、Ｍ
ｎ ： ０．４〜５％、Ｎｉ ； ０．５〜４．５％、
Ｃｒ；１５〜１８．５％、Ｍｏ：２〜４％、Ｃｏ；３．
５〜７％、残部が実質的にＦｓよりなり、Ｎｉ当量；１
８〜２４ 、Ｃｒ＋３．３Ｍｏ ； ２１．６〜２９
％、フェライト相；０．５〜３０％、マルテンサイト相
；４０％以下、残部がオーステナイト相あるいはイプシ
ロン相であることを特徴とするもので、耐キャビテーシ
ョン・エロージヨン性と耐海水腐食性に優れるとともに
鋳造性・溶接性が良好なものである。The stainless steel cast copper of the present invention (hereinafter referred to as the first invention) is C
; 0.05-0.1%, Si; 0.1-1.5%, M
n: 0.4-5%, Ni; 0.5-4.5%,
Cr; 15-18.5%, Mo: 2-4%, Co; 3.
5 to 7%, the remainder substantially consists of Fs, Ni equivalent: 1
8-24, Cr+3.3Mo; 21.6-29
%, ferrite phase: 0.5-30%, martensitic phase: 40% or less, and the remainder is austenite phase or epsilon phase, and has excellent cavitation/erosion resistance and seawater corrosion resistance. It has good castability and weldability.
また、他の発明（以下第２の発明という）のステンレス
鋳鋼はＣ： ０．１〜０．２２％１８１：０．１〜１．
５％、Ｍｎ；Ｑ、４〜５％、Ｎｉ；０．５〜４．５％、
Ｃｒ ：１５〜１８．５％１ＭＯ；２〜４％、Ｃｏ ；
３．５〜７％、残部が実質的にＦｅよりなり、Ｎｉ当
量； １８〜２６ 、Ｃｒ＋３．３Ｍｏ ： ２１．
６〜２９％、フェライト相；０．５〜３０％、マルテン
サイト相：４０％以下、残部がオーステナイト相あるい
はイプシロン相であることを特徴とするもので、耐海水
腐食性において第１の発明の鋳鋼よりやや劣るが、耐キ
ャビテーション性では第１の発明の鋳鋼より優れるもの
である。Further, the stainless steel cast steel of another invention (hereinafter referred to as the second invention) has C: 0.1 to 0.22% 181:0.1 to 1.
5%, Mn; Q, 4-5%, Ni; 0.5-4.5%,
Cr: 15-18.5% 1MO; 2-4%, Co;
3.5 to 7%, the balance substantially consisting of Fe, Ni equivalent: 18 to 26, Cr+3.3Mo: 21.
6 to 29%, ferrite phase: 0.5 to 30%, martensite phase: 40% or less, and the remainder is an austenite phase or an epsilon phase, and has the first invention in terms of seawater corrosion resistance. Although it is slightly inferior to cast steel, it is superior to the cast steel of the first invention in terms of cavitation resistance.
さらに他の発明（以下第３の発明という）のステンレス
鋳鋼はＣ： ０．０１〜０．１％９８１：０．１〜１．
５％、Ｍｎ；０．４〜５％、Ｎｉ；０．５〜４．５％、
Ｃｒ ； １５〜１８．５％９Ｍｏ；２〜４％、Ｃｏ
； ３．５〜７％、ＮＯ，０１〜０．１５％、残部が実
質的にＦｅよりなり、Ｎｉ当量；１８〜２６ 、Ｃｒ
＋３．３Ｍｏ：２１．６〜２９％、フェライト相；０．
５〜３０％、マルテンサイト相；４０％以下、残部がオ
ーステナイト相あるいはイプシロン相であることを特徴
とするもので、鋳造性・溶接性において第１の発明の鋳
鋼よりやや劣るものの耐海水腐食性に第１の発明の鋳鋼
より優れるものである。Furthermore, the stainless steel cast steel of another invention (hereinafter referred to as the third invention) has C: 0.01-0.1%981:0.1-1.
5%, Mn; 0.4-5%, Ni; 0.5-4.5%,
Cr; 15-18.5% 9Mo; 2-4%, Co
; 3.5-7%, NO, 01-0.15%, the balance substantially consists of Fe, Ni equivalent: 18-26, Cr
+3.3Mo: 21.6-29%, ferrite phase; 0.
5 to 30%, martensitic phase; 40% or less, the remainder is austenite phase or epsilon phase, and although it is slightly inferior to the cast steel of the first invention in castability and weldability, it has seawater corrosion resistance. This is superior to the cast steel of the first invention.
次に、成分組成および金属組織を限定した理由を述べる
。Next, the reason for limiting the component composition and metal structure will be described.
（Ｃ）
０．０５％以下では耐キャビテーション・エロージヨン
性の優れた鋳鋼が得られない。また、０．１ ％以上で
は６００〜ｂ
ｈｒの熱処理範囲でオーステナイト粒界およびオーステ
ナイト〜フェライト粒界にそって、また５００〜６００
℃Ｘ （１〜１Ｏ）ｈｒの熱処理範囲でマルテンサイト
葉にそって選択腐食（粒界腐食）が見られ、腐食はＣ含
有量が増す程激しくなる。よって０．０５〜０．１％添
加する。(C) If it is less than 0.05%, cast steel with excellent cavitation and erosion resistance cannot be obtained. In addition, when it is 0.1% or more, in the heat treatment range of 600 to 600 b hr, along the austenite grain boundaries and austenite to ferrite grain boundaries, and 500 to 600 b hr.
Selective corrosion (intergranular corrosion) is observed along the martensite leaves in the heat treatment range of ℃X (1 to 1 O) hr, and the corrosion becomes more severe as the C content increases. Therefore, add 0.05 to 0.1%.
しかし、第１の発明の鋳鋼より耐海水腐食性にやや劣り
、耐キャビテーション・エロージヨン性では優れた鋳鋼
を得たい場合、Ｃ含有量は少なく０．１〜０．２２％添
加する。また、鋳造性・溶接性においてやや劣るものの
耐海水腐食性において第１の発明より優れた鋳鋼を得た
い場合、０．０１〜０．０５添加する。However, if it is desired to obtain a cast steel that is slightly inferior to the cast steel of the first invention in seawater corrosion resistance but superior in cavitation and erosion resistance, the C content is added at a low level of 0.1 to 0.22%. Moreover, when it is desired to obtain a cast steel which is slightly inferior in castability and weldability but superior in seawater corrosion resistance to the first invention, 0.01 to 0.05 of C is added.
（Ｓｉ）
ＣｒおよびＭｏの含有量を増加させ、耐海水腐食性を確
保、同時にＮｉ当量の増大を抑制するためにＮｉ当量元
素であるＳｉは少ない程良い。しかし鋳造性を確保する
必要であるので、０．１〜１．５％添加する。(Si) In order to increase the contents of Cr and Mo, ensure seawater corrosion resistance, and at the same time suppress the increase in Ni equivalent, the smaller the amount of Si, which is the Ni equivalent element, the better. However, since it is necessary to ensure castability, it is added in an amount of 0.1 to 1.5%.
（Ｍｎ）
Ｓｉと同様の理由により少ない程良い。一方、硬質の加
工誘起マルテンサイト相を得るには多量に添加すること
が好ましい。またＮｉ当量との関係を守る必要があり、
０．４〜５ ％添加する。(Mn) For the same reason as Si, the smaller the amount, the better. On the other hand, in order to obtain a hard deformation-induced martensitic phase, it is preferable to add a large amount. Also, it is necessary to protect the relationship with Ni equivalent.
Add 0.4-5%.
（Ｎ ｉ ）
添加理由はＭｎと同様である。一方、耐海水腐食性を向
上させる上で必要である。０．５ ％以下では溶解素材
の選定上実用的でない。よって０．５〜４．５ ％添加
する。(N i ) The reason for addition is the same as that for Mn. On the other hand, it is necessary to improve seawater corrosion resistance. If it is less than 0.5%, it is not practical in terms of selecting a melting material. Therefore, add 0.5 to 4.5%.
（Ｃｒ）
Ｎｉ当量およびＣｒ＋３．３Ｍｏ量を確保する上で必要
である。また、１５％以下では耐海水腐食性が著しく損
なわれると共にδ−フェライト相が増大してオーステナ
イト相が減少するので、加工誘起マルテンサイト相へ生
成量が少なくなる。(Cr) Necessary to ensure Ni equivalent and Cr+3.3Mo amount. Moreover, if it is less than 15%, the seawater corrosion resistance is significantly impaired, and the δ-ferrite phase increases and the austenite phase decreases, so that the amount of deformation-induced martensite phase produced decreases.
１８．５％以上では適正Ｎｉ当量を確保しながらＭｏを
添加することが回置となる。よって１５〜１８．５％添
加する。At 18.5% or more, Mo must be added while ensuring an appropriate Ni equivalent. Therefore, add 15 to 18.5%.
（Ｍｏ）
添加理由はＣｒと同様である。２％以下では耐海水腐食
性が著しく損なわれる。また、４％以上では耐海水腐食
性の効果が飽和し経済的でない。(Mo) The reason for addition is the same as that for Cr. If it is less than 2%, seawater corrosion resistance will be significantly impaired. Moreover, if it exceeds 4%, the effect of seawater corrosion resistance is saturated and it is not economical.
よって２〜４％添加する。Therefore, add 2 to 4%.
（Ｇｏ）
耐キャビテーション・エロージヨン性の向上に顕著な効
果があるが７％以上添加しても効果は飽和し経済的では
ない、また３、５％以下では効果が乏しい、よって、３
．５〜７％添加する。(Go) It has a remarkable effect on improving cavitation and erosion resistance, but if it is added in an amount of 7% or more, the effect is saturated and it is not economical.If it is less than 3.5%, the effect is poor.
．． Add 5-7%.
（Ｎ）
Ｃｏの添加理由と同様、オーステナイト相の安定に有効
であるが加工誘起マルテンサイトの生成を促進すると共
に、耐海水腐食性の向上に有効である。Ｎを添加する場
合、Ｃは０．０１−０．０５％の添加にとどめる。Ｉ’
ｌｔ０．０１％以下では耐海水腐食性に効果がなく、０
．１５％以上では固ｉ容化熱処理温度域で固溶限以上と
なり耐海水腐食性が低下する。よって０．０１〜０．１
５％添加する。(N) Same as the reason for adding Co, it is effective for stabilizing the austenite phase, promotes the formation of deformation-induced martensite, and is effective for improving seawater corrosion resistance. When N is added, the amount of C added is limited to 0.01-0.05%. I'
If it is less than 0.01%, there is no effect on seawater corrosion resistance, and 0.
．． If it is more than 15%, the solid solubility limit will be exceeded in the solid-solidification heat treatment temperature range, resulting in a decrease in seawater corrosion resistance. Therefore, 0.01 to 0.1
Add 5%.
０．５％以下では鋳造時および溶接時に高温割れが発生
する。また、３０％以上ではオーステナイト相が少なく
、加工誘起マルテンサイト相の生成量が原理的に多くと
れず耐キャビテーション・エロージヨン性の向上が期待
できない、よって０．５〜３０％とした。If it is less than 0.5%, hot cracking will occur during casting and welding. Moreover, if it is 30% or more, the austenite phase is small and the amount of deformation-induced martensite phase produced cannot be expected to be large in principle, and improvement in cavitation and erosion resistance cannot be expected.Therefore, it is set at 0.5 to 30%.
４０％以上では、Ｎｉ当量が１６〜１８である場合、加
工誘起マルテンサイト相の生成量が減少し、耐キャビテ
ーション・エロージヨン性が向上しない。よって４０％
以下とした。When the Ni equivalent is 40% or more and the Ni equivalent is 16 to 18, the amount of deformation-induced martensitic phase produced decreases, and the cavitation and erosion resistance does not improve. Therefore 40%
The following was made.
次に本発明の詳細な説明するが、説明に先立ち本発明の
基本的な考え方を説明する。Next, the present invention will be explained in detail, but prior to the explanation, the basic idea of the present invention will be explained.
成を示す。表より材料＆Ａ、Ｂ、Ｃ，ＤおよびＥはＣｏ
含有量がそれぞれほぼ０％、２％、４％。Indicates completion. From the table, materials &A, B, C, D and E are Co
The content is approximately 0%, 2%, and 4%, respectively.
６％および８％である。また材料ＦはＣｏ：６％でＮが
添加しである。これらの材料のキャビテーション・エロ
ージョン特性（壊食量）および腐食減量は表に示すとう
りである。6% and 8%. Further, material F has Co: 6% and N is added. The cavitation/erosion characteristics (erosion amount) and corrosion loss of these materials are shown in the table.
次に第１表のキャビテーション・エロージョンを
試験結果を第１図にまとめ島よ。ここでは、材料Ｎα毎
にＣ含有量とＮｉ当量に対する壊食量を４段階に分類し
て示した。図より、Ｃｏ：０％の場合における壊食量は
、Ｃ含有量が高く、Ｎｉ当量が２２以下の場合、概略４
０■以下となるものの、Ｃ含有量が０．１％、Ｎｉ当量
が２２以上では４０■以上であることがわかる。一方、
Ｃｏ含有量が２％、４％、６％および８％と増すに伴い
、Ｃ含有量とＮｉ当量の関係において、壊食量の低下が
見られる。そして、これらの測定値より、予想される各
壊食量レベルのバンド、たとえば１０〜２０■（図中Δ
印）はＣｏ含有量が６％の場合、最も低Ｃ含有量側に位
置している。また、キャビテーション試験後の材料硬さ
をその断面より測定した。その結果、表面より０．０２
１の位置における硬さは、壊食量の小さい材料程硬く、
最大でＨｙ＝６３０にも達していた。この傾向はＮｉ当
量が１８〜２４で、Ｃ含有量の高い程顕著であった。ま
た、Ｃ含有量が同じ時はＮｉ当量が２１に近づく程、Ｃ
含有量とＮｉ当量が同等の時はＣ。Next, the cavitation/erosion test results in Table 1 are summarized in Figure 1. Here, the amount of erosion relative to the C content and Ni equivalent is classified into four levels for each material Nα. From the figure, the amount of erosion in the case of Co: 0% is approximately 4 when the C content is high and the Ni equivalent is 22 or less.
It can be seen that although the value is 0 ■ or less, it is 40 ■ or more when the C content is 0.1% and the Ni equivalent is 22 or more. on the other hand,
As the Co content increases to 2%, 4%, 6%, and 8%, the amount of erosion decreases in the relationship between the C content and Ni equivalent. From these measured values, bands of each expected erosion amount level, for example, 10 to 20
) is located on the lowest C content side when the Co content is 6%. In addition, the material hardness after the cavitation test was measured from its cross section. As a result, 0.02
The hardness at position 1 is as follows: The smaller the amount of erosion, the harder the material.
The maximum value reached Hy=630. This tendency was more pronounced as the Ni equivalent was 18 to 24 and the C content was higher. Also, when the C content is the same, the closer the Ni equivalent is to 21, the more C
C when the content and Ni equivalent are the same.
含有量が６％に近づく程、共に硬さが高く、耐キャビー
テヨン・エロージヨン性と良い相関が見られた。次に金
属組織変化に注目すると、Ｎｉ当量が２４から大きくな
るに伴ない試験前後共にオーステナイト相が安定に存在
するものの、Ｎｉ当量が２１前後では試験前大部分オー
ステナイト相であっても、試験後９０％以上マルテンサ
イト相になっていた。Ｎｉ当量が１８以下では試験前に
おいて大部分マルテンサイト相であり、試験後マルテン
サイト相が多少増すにとどまっていた。そして、この傾
向はＣｏ含有量が４〜８％、なかでも６％のとき最も顕
著であった。The closer the content was to 6%, the higher the hardness, and a good correlation with cavity resistance and erosion resistance was observed. Next, focusing on changes in metallographic structure, as the Ni equivalent increases from 24, an austenite phase stably exists both before and after the test, but when the Ni equivalent is around 21, even though most of the phase is austenite before the test, after the test More than 90% was in the martensite phase. When the Ni equivalent was 18 or less, the martensite phase was mostly present before the test, and the martensite phase only slightly increased after the test. This tendency was most remarkable when the Co content was 4 to 8%, especially 6%.
以上の事実は耐キャビテーション・エロージヨン性が主
にＣ含有量と材料のマルテンサイト相変態能によって決
定されることを示しており、キャビテーション衝撃によ
って材料が加工を受けた時。The above facts indicate that the cavitation and erosion resistance is mainly determined by the C content and martensitic phase transformation ability of the material, and when the material is processed by cavitation impact.
硬い硬化層の生成しやすい材料が優れた耐キャビ−チー
ジョン・エロージヨン性を示すものと判断される。そし
て、Ｃは一定量の加工誘起マルテンサイト相が生成した
場合、その硬さ上昇に有効に作用し、Ｎｉ当量は加工誘
起マルテンサイト相の生成しやすさくＮｉ当量最大の場
合、オーステナイト相が安定、Ｎｉ当量が小の場合、当
初よりマルテンサイト相あるいはフェライト相で共に有
効がない）に作用するものと思われる。またＣＯはオー
ステナイト相生成元素でありながらＭｄ点の低下割合が
小さく、オーステナイト相生成範囲を拡大すると共に、
加工誘起マルテンサイト生成範囲を増大する。また本材
料に０．４〜５．０％添加した。Ｍｎの効果は良く知ら
れているように、加工誘起マルテンサイト相の硬さ上昇
に有効な作用がある。よって、Ｃ以外については第１の
発明および第２の発明に示す合金組成が耐キャビテーシ
ョン・エロージヨン性に有効である。It is considered that materials that easily form a hard hardened layer exhibit excellent cavity corrosion and erosion resistance. Furthermore, when a certain amount of deformation-induced martensitic phase is generated, C effectively acts to increase the hardness, and Ni equivalent facilitates the formation of deformation-induced martensitic phase, and when the Ni equivalent is maximum, the austenite phase becomes stable. , it is thought that when the Ni equivalent is small, the martensitic phase or the ferrite phase are both ineffective from the beginning. In addition, although CO is an austenite phase forming element, the rate of decrease in the Md point is small, and it expands the range of austenite phase formation.
Increase the range of deformation-induced martensite formation. Moreover, 0.4 to 5.0% was added to this material. As is well known, the effect of Mn is effective in increasing the hardness of the deformation-induced martensitic phase. Therefore, except for C, the alloy compositions shown in the first invention and the second invention are effective in cavitation and erosion resistance.
次に耐食性について述べる。第１表に示した腐食減量を
整理して第２図に示す。ここではＧｏＣ含有量、６％の
場合について示した。第２図より、腐食減量は。ｒ’３
、３ Ｍ。量およびオー８．−ケイ。Next, we will discuss corrosion resistance. The corrosion loss shown in Table 1 is summarized and shown in Figure 2. Here, the case where the GoC content is 6% is shown. From Figure 2, the corrosion loss is. r'3
, 3M. Amount and O8. -Kay.
相合有量でよく整理され、Ｃｒ＋３．３Ｍｏ量およびオ
ーステナイト相含有量が６０％以上の場合、Ｃｒ ＋
３ 、３ Ｍ ｏ量が２１．６％以上で５Ｃ８１３相当
以上の耐食性が得られる。以上のことはＣＯＣ含有量４
〜８％であってもほぼ同様であった。Well organized by interlocking content, when the amount of Cr + 3.3Mo and the content of austenite phase is 60% or more, Cr +
When the amount of 3,3Mo is 21.6% or more, corrosion resistance equivalent to or higher than that of 5C813 can be obtained. The above is COC content 4
It was almost the same even when it was 8%.
また、Ｃ含有量については、０．１％以上では６００〜
７５０℃Ｘ １〜１０ ｈ ｒの熱処理範囲でオーステ
ナイト粒界およびオーステナイト−フェライト粒界にそ
って、５００〜ｂ
１０ｈｒの熱処理範囲でマルテンサイト葉にそって選択
腐食（粒界腐食）が見られ、Ｃ含有量が増す程、激しく
腐食する。また、Ｃ固溶限の０．１５％以上では固溶化
処理材でさえ、オーステナイト粒界にそった選択腐食が
見られる。In addition, regarding the C content, if it is 0.1% or more, it is 600~
Selective corrosion (intergranular corrosion) was observed along the austenite grain boundaries and austenite-ferrite grain boundaries in the heat treatment range of 750°C for 1 to 10 hours, and along the martensite leaves in the heat treatment range of 500 to 10 hours. The higher the C content, the more intense the corrosion. Further, at 0.15% or more of the C solid solubility limit, selective corrosion is observed along the austenite grain boundaries even in the solution treated material.
以上より、耐キャビテーション・エロージヨン性および
耐海水腐食性を満足するためには、Ｃ；０．０５〜０．
１０％が望ましく、耐海水腐食性の多少の低下が許され
る場合にはＣ：０．１〜０．２２％添加する１本鋳鋼は
耐キャビテーション・エロージヨン性では第１の発明の
鋳鋼より優れる。また耐海水腐食のさらに優れた鋳鋼を
得たい場合にはＣ； ０．０１〜０．０５％添加する。From the above, in order to satisfy cavitation/erosion resistance and seawater corrosion resistance, C; 0.05 to 0.
10% is desirable, and if a slight decrease in seawater corrosion resistance is allowed, a single cast steel containing 0.1 to 0.22% C is superior to the cast steel of the first invention in terms of cavitation and erosion resistance. In addition, when it is desired to obtain cast steel with even better seawater corrosion resistance, C is added in an amount of 0.01 to 0.05%.
つぎに本発明の具体的実施例を説明する。Next, specific examples of the present invention will be described.
前述の考え方を基にして作成した本発明の鋳鋼の化学生
成と測定結果を第２表に示す、 Ｉ−１゜−２が第１の
発明に係る鋳鋼、Ｈ−１，−２が第２の発明に係る鋳鋼
、ｌｌ−１，−２が第３の発明に係る鋳鋼をそれぞれ示
す、キャビテーション・エロージョン試験は電歪振動式
キャビテーション・エロージョン試験装置を用い、６
、３ Ｋ ＨＸ１２０μｍ振幅、２５℃の３％食塩水中
で２時間試験して求めた。鋳鋼の大きなキャビテーショ
ンに接する面積が３．８ｄである。腐食試験は耐海水腐
食性２の相関性が良い０．８％ＦｅＣａａ＋０．５％Ｈ
ＣＱ溶液であり、室温で１２００ｈ ｒ浸漬し重量減に
より求めた。鋳鋼の大きな２０Ｘ３０Ｘ３ｔで耐キャビ
テーション・エロージヨン性を示す壊食量および腐食減
量の測定結果を前記第２表に示す。表より明らかなよう
に、壊食量、腐食減量ともに優れている。The chemical formation and measurement results of the cast steel of the present invention created based on the above-mentioned idea are shown in Table 2. I-1゜-2 is the cast steel according to the first invention, H-1 and -2 are the second cast steel The cavitation/erosion test was conducted using an electrostrictive vibration type cavitation/erosion testing device.
, 3 K H x 120 μm amplitude, 2 hours in 3% saline at 25° C. The area in contact with the large cavitation of cast steel is 3.8d. Corrosion test is 0.8%FeCaa + 0.5%H with good correlation of seawater corrosion resistance 2
It is a CQ solution and was determined by weight loss after immersion at room temperature for 1200 hours. Table 2 above shows the measurement results of the amount of erosion and corrosion weight loss showing the cavitation and erosion resistance of a large 20x30x3t cast steel. As is clear from the table, both the amount of erosion and the amount of corrosion loss are excellent.
以上説明したように本発明によれば、耐キャビテーショ
ン・エロージヨン性を耐海水腐食性に優れるとともに鋳
造性・溶接性も良好なステンレス情調が得られ１本鋳鋼
を例えば海水ポンプのインペラ材料として使用すればそ
の寿命が向上する。As explained above, according to the present invention, a stainless steel material with excellent cavitation and erosion resistance and seawater corrosion resistance as well as good castability and weldability can be obtained, and single cast steel can be used as an impeller material for a seawater pump, for example. Improves the lifespan of grass.
Claims (1)
、Ｍｎ；０．４〜５％、Ｎｉ；０．５〜４．５％、Ｃｒ
；１５〜１８．５％、Ｍｏ；２〜４％、Ｃｏ；３．５〜
７％、残部が実質的にＦｅよりなり、Ｎｉ当量〔Ｎｉ％
＋０．６５Ｃｒ％＋０．９８Ｍｏ％＋１．０５Ｍｎ％＋
０．３５Ｓｉ％＋１２．６Ｃ％〕；１８〜２４、Ｃｒ＋
３．３Ｍｏ；２１．６〜２９％、フェライト相；０．５
〜３０％、マルテンサイト相；４０％以下、残部がオー
ステナイト相あるいはイプシロン相であることを特徴と
する耐キャビテーション・エロージヨン性と耐海水腐食
性に優れたステンレス鋳鋼。 ２、Ｃ；０．１〜０．２２％、Ｓｉ；０．１〜１．５％
、Ｍｎ；０．４〜５％、Ｎｉ；０．５〜４．５％、Ｃｒ
；１５〜１８．５％、Ｍｏ；２〜４％、Ｃｏ；３．５〜
７％、残部が実質にＦｅよりなり、Ｎｉ当量〔Ｎｉ％＋
０．６５Ｃｒ％＋０．９８Ｍｏ％＋１．０５Ｍｎ％＋０
．３５Ｓｉ％＋１２．６Ｃ％〕；１８〜２６、Ｃｒ＋３
．３Ｍｏ；２１．６〜２９％、フェライト相；０．５〜
３０％、マルテンサイト相；４０％以下、残部がオース
テナイト相あるいはイプシロン相であることを特徴とす
る耐キャビテーション・エロージヨン性と耐海水腐食性
に優れたステンレス鋳鋼。 ３、Ｃ；０．０１〜０．５％、Ｓｉ；０．１〜１．５％
、Ｍｎ；０．４〜５％、Ｎｉ；０．５〜４．５％、Ｃｒ
；１５〜１８．５％、Ｍｏ；２〜４％、Ｃｏ；３．５〜
７％、Ｎｉ０．０１〜０．１５％、残部が実質的にＦｅ
よりなり、Ｎｉ当量〔Ｎｉ％＋０．６５Ｃｒ％＋０．９
８Ｍｏ％＋１．０５Ｍｎ％＋０．３５Ｓｉ％＋１２．６
Ｃ％〕；１８〜２６、Ｃｒ＋３．３Ｍｏ；２１．６〜２
９％、フェライト相；０．５〜３０％、マルテンサイト
相；４０％以下、残部がオーステナイト相あるいはイプ
シロン相であることを特徴とする耐キャビテーション・
エロージヨン性と耐海水腐食性に優れたステンレス鋳鋼
。[Claims] 1, C: 0.05-0.1%, Si: 0.1-1.5%
, Mn; 0.4-5%, Ni; 0.5-4.5%, Cr
; 15-18.5%, Mo; 2-4%, Co; 3.5-
7%, the remainder essentially consists of Fe, and the Ni equivalent [Ni%
+0.65Cr%+0.98Mo%+1.05Mn%+
0.35Si%+12.6C%]; 18-24, Cr+
3.3Mo; 21.6-29%, ferrite phase; 0.5
A stainless steel cast steel with excellent cavitation/erosion resistance and seawater corrosion resistance, characterized by ~30% martensitic phase; 40% or less, the remainder being austenite phase or epsilon phase. 2, C; 0.1-0.22%, Si; 0.1-1.5%
, Mn; 0.4-5%, Ni; 0.5-4.5%, Cr
; 15-18.5%, Mo; 2-4%, Co; 3.5-
7%, the remainder essentially consists of Fe, and the Ni equivalent [Ni%+
0.65Cr%+0.98Mo%+1.05Mn%+0
．． 35Si%+12.6C%]; 18-26, Cr+3
．． 3Mo; 21.6-29%, ferrite phase; 0.5-29%
Stainless steel cast steel with excellent cavitation/erosion resistance and seawater corrosion resistance, characterized by 30% martensitic phase; 40% or less, the remainder being austenite phase or epsilon phase. 3, C; 0.01-0.5%, Si; 0.1-1.5%
, Mn; 0.4-5%, Ni; 0.5-4.5%, Cr
; 15-18.5%, Mo; 2-4%, Co; 3.5-
7%, Ni 0.01-0.15%, remainder substantially Fe
The Ni equivalent [Ni%+0.65Cr%+0.9
8Mo%+1.05Mn%+0.35Si%+12.6
C%]; 18-26, Cr+3.3Mo; 21.6-2
9%, ferrite phase; 0.5-30%, martensitic phase; 40% or less, the remainder being austenite phase or epsilon phase.
Cast stainless steel with excellent erosion and seawater corrosion resistance.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP14940484A JPS6130655A (en) | 1984-07-20 | 1984-07-20 | Stainless cast steel having superior resistance to cavitation erosion and corrosion by seawater |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP14940484A JPS6130655A (en) | 1984-07-20 | 1984-07-20 | Stainless cast steel having superior resistance to cavitation erosion and corrosion by seawater |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS6130655A true JPS6130655A (en) | 1986-02-12 |
| JPH0517301B2 JPH0517301B2 (en) | 1993-03-08 |
Family
ID=15474388
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP14940484A Granted JPS6130655A (en) | 1984-07-20 | 1984-07-20 | Stainless cast steel having superior resistance to cavitation erosion and corrosion by seawater |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS6130655A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS62189284A (en) * | 1986-02-17 | 1987-08-19 | 日産自動車株式会社 | Window regulator of sashless door for car |
| US6943317B1 (en) | 2004-07-02 | 2005-09-13 | Advanced Energy Industries, Inc. | Apparatus and method for fast arc extinction with early shunting of arc current in plasma |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5054515A (en) * | 1973-09-14 | 1975-05-14 | ||
| JPS5170120A (en) * | 1974-12-16 | 1976-06-17 | Mitsubishi Steel Mfg | KOCHORYOKUSUTENRESUKO |
| JPS5837162A (en) * | 1981-08-31 | 1983-03-04 | Toshiba Corp | Pump and its manufacture |
-
1984
- 1984-07-20 JP JP14940484A patent/JPS6130655A/en active Granted
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5054515A (en) * | 1973-09-14 | 1975-05-14 | ||
| JPS5170120A (en) * | 1974-12-16 | 1976-06-17 | Mitsubishi Steel Mfg | KOCHORYOKUSUTENRESUKO |
| JPS5837162A (en) * | 1981-08-31 | 1983-03-04 | Toshiba Corp | Pump and its manufacture |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS62189284A (en) * | 1986-02-17 | 1987-08-19 | 日産自動車株式会社 | Window regulator of sashless door for car |
| US6943317B1 (en) | 2004-07-02 | 2005-09-13 | Advanced Energy Industries, Inc. | Apparatus and method for fast arc extinction with early shunting of arc current in plasma |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0517301B2 (en) | 1993-03-08 |
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