JPS581062A - Corrosion- and abrasion-resistant cast steel - Google Patents
Corrosion- and abrasion-resistant cast steelInfo
- Publication number
- JPS581062A JPS581062A JP9934181A JP9934181A JPS581062A JP S581062 A JPS581062 A JP S581062A JP 9934181 A JP9934181 A JP 9934181A JP 9934181 A JP9934181 A JP 9934181A JP S581062 A JPS581062 A JP S581062A
- Authority
- JP
- Japan
- Prior art keywords
- ferrite
- corrosion
- steel
- cast steel
- wear
- 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.)
- Pending
Links
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- Heat Treatment Of Steel (AREA)
Abstract
Description
【発明の詳細な説明】 本発明は鋳造性に優れ、腐食環境下に於いて。[Detailed description of the invention] The present invention has excellent castability in corrosive environments.
優れた耐食耐摩耗性を有するフェライト−オーステナイ
ト型二相ステ/レス鋳鋼に係るものである。The present invention relates to a ferrite-austenite type two-phase steel/less cast steel having excellent corrosion and wear resistance.
最近の省資源、省エネルギーの要求により低品位油や石
炭を応用する技術が増加し、排脱装置や重質油2石炭の
輸送/ステムのような中で。Due to recent demands for resource and energy conservation, technologies that apply low-grade oil and coal are increasing, such as in removal equipment and transport/stems for heavy oil and coal.
腐食性を有するスラリーを移動させるボjグのような機
器は腐食と共に摩耗が問題になっている。従来かかる部
材用材料としては: 5O814(オーステナイト鋳
鋼)やSO811オーステナイト−フェライト2相ステ
ンレス鋳鋼が使用されていたがこれら材料は耐食性の点
では問題は少ないが硬さが低く、耐摩耗性については全
く考慮されていないために、最近の腐食及び摩耗環境の
苛酷化により短時間の使用で摩耗による補修或いは廃却
が行なわれている。また高(]「鋳鉄のような耐摩耗材
料は腐食の方で減肉が進行し耐摩耗性と共に耐食性を備
えた材料が要求されている。従って、従来の腐食材料の
耐摩耗性向上の方法として、 80811のようなオ
ーステナイト−フェライト2相ステンレス鋳鋼について
は。Equipment such as bogs that move corrosive slurry suffer from corrosion and wear. Conventionally, materials for such parts include: 5O814 (austenitic cast steel) and SO811 austenitic-ferritic duplex stainless steel cast steel, but these materials have few problems in terms of corrosion resistance, but have low hardness and have no wear resistance. Because of this lack of consideration, recent corrosion and abrasion environments have become more severe, leading to repair or scrapping due to wear after a short period of use. In addition, wear-resistant materials such as cast iron undergo thinning due to corrosion, and materials with both wear and corrosion resistance are required.Therefore, conventional methods for improving the wear resistance of corroding materials are needed. For austenitic-ferritic duplex stainless cast steels such as 80811.
600〜700℃に加熱しフェライトの部分を(
ソゲI相化させることによって硬化させる材料が検討さ
れているが、材質的に非常に脆化するために機器部材と
しての適用が制限されると共脱落と共に進行するので硬
さが高い制には耐摩耗性の改善が少ない。Materials that harden the ferrite by heating it to 600 to 700°C to turn it into the Soge I phase have been considered, but the material is extremely brittle, which limits its application as equipment components. Since the wear progresses with the shedding, there is little improvement in wear resistance for hardness steels.
本発明は以上のような従来の耐食材料に加え耐摩耗を賦
与した耐食耐摩耗鋳鋼に関する提案で、co1%以下、
S、i 0.5〜1.5%、Mn0.5−15%lC
「22〜28%、N16〜11%、Mo1.5〜35%
、 Ou 2. O〜5.0%、残部Fa及び不純物か
ら成り、かつフェライトの体積率が50〜65チで、こ
れを900〜1100℃で溶体化処理後、450〜55
0℃の析出硬化処理がなされてなることを特徴とする2
相ステ/レス系耐食耐摩耗鋳鋼で1本発明によって従来
のオーステナイト系鋳鋼(SO8−14)或いは2相ス
テンレス鋳鋼(scs −11)に比べ耐食性は同等で
耐摩耗性が2〜3倍優れる材料が得られた。The present invention is a proposal for a corrosion-resistant and wear-resistant cast steel that is added with wear resistance in addition to the conventional corrosion-resistant materials as described above.
S, i 0.5-1.5%, Mn 0.5-15% lC
"22-28%, N16-11%, Mo1.5-35%
, Ou 2. O ~ 5.0%, the balance consists of Fa and impurities, and the volume fraction of ferrite is 50 ~ 65 cm, and after solution treatment at 900 ~ 1100 ° C., 450 ~ 55%
2 characterized by being subjected to precipitation hardening treatment at 0°C.
A material that has the same corrosion resistance and 2 to 3 times better wear resistance than conventional austenitic cast steel (SO8-14) or duplex stainless steel cast steel (SCS-11) due to the present invention. was gotten.
次に本発明に於ける限定理由について説明する。Cは出
来るだけ少ない方が耐食性を維持するために望ましく、
o1%を越えると従来の材料と同様に耐食性を劣化させ
る。Siは有効な脱酸剤であり通常の製鋼過程に於いて
必然的に含有されるものであるがあまり多量に含有させ
るとジグI相の生成傾向を大にし、材料を脆化させるた
めに05〜15%とした。MnもSiと同様製鋼過程に
於ける脱酸や鋳造過程の流動性を維持させる元素で通常
の範囲05〜15チである。Next, the reasons for limitations in the present invention will be explained. It is desirable to have as little C as possible in order to maintain corrosion resistance.
If it exceeds 1%, the corrosion resistance deteriorates as with conventional materials. Si is an effective deoxidizing agent and is inevitably included in the normal steelmaking process, but if it is included in too much, it increases the tendency to form the Jig I phase and makes the material brittle. ~15%. Like Si, Mn is an element that maintains fluidity during deoxidation during the steel manufacturing process and during the casting process, and has a normal range of 05 to 15%.
Orは耐食性を維持させる重要元素で、耐食性を高める
だめには含有量が多い方が望ましいが28チを越えると
溶体化処理時の冷却速度によってのおそれがない範囲で
出来るだけ多く、シかも。Or is an important element for maintaining corrosion resistance, and in order to improve corrosion resistance, it is desirable to have a high content, but if it exceeds 28%, it may be as much as possible without causing any risk due to the cooling rate during solution treatment.
Ni 、 Cu量とのかねあいで本発明の特徴であるフ
ェライト体積率50〜65%を維持する含有量として2
2〜28チを限定した。狛は、優れた耐摩耗性を有する
フェライト体積率50〜65チを保つために先に示した
C「含有量とのかねあいで6〜11チが必要である。M
oはC【との共存によって局部的耐食性を著るしく向上
させる元素で本発明も従来合金と同様15〜35%含有
するものである。Cuは本発明合金の析出硬化性を与え
る元素でオーステナイト中には多量に含有するが、フェ
ライト相中には固溶度が少なく。2 as the content that maintains the ferrite volume fraction of 50 to 65%, which is a feature of the present invention, in balance with the amount of Ni and Cu.
Limited to 2 to 28 inches. In order to maintain a ferrite volume fraction of 50 to 65 inches, which has excellent abrasion resistance, 6 to 11 inches of ferrite is required in consideration of the above-mentioned C content.M
O is an element that significantly improves local corrosion resistance when coexisting with C, and the present invention also contains 15 to 35% of the same as in the conventional alloy. Cu is an element that imparts precipitation hardenability to the alloy of the present invention, and is contained in large amounts in austenite, but its solid solubility in the ferrite phase is low.
Cu−rich相(e相)を析出し析出硬化を起す。A Cu-rich phase (e-phase) is precipitated and precipitation hardening occurs.
従って析出硬化による耐摩耗性を維持するためにはフェ
ライト量の影響が大きく2本発明に於けるフェライト体
積率50〜65%に於いて適当な析出硬化性と優れた耐
摩耗性が得られその範囲としてはCu2〜5チで、2チ
以下では析出硬化能が充分でなく、捷だ5チ以上では+
、 Ou +rich相が塊状に析出し靭性低下が大き
く孔食状に腐食及び摩耗が発生し耐摩耗性が低下する。Therefore, in order to maintain wear resistance due to precipitation hardening, the amount of ferrite has a large influence.2 Appropriate precipitation hardenability and excellent wear resistance can be obtained at a ferrite volume ratio of 50 to 65% in the present invention. The range is 2 to 5 Cu, less than 2 Cu does not have sufficient precipitation hardening ability, and Cu is more than 5 Cu.
, the Ou+rich phase precipitates in lumps, significantly reducing toughness, causing pitting-like corrosion and wear, and reducing wear resistance.
フェライト体積率は本発明合金の析出硬化能を決定し1
.耐摩耗性に大きな影響を与えるもので、フェライト量
が少ない場合充分な析出硬化能が得られないため耐摩耗
性が充分でなく、まヌ
た多い場合は析出硬化と共に/グオ相化し脆弱になると
共に基地と析出相関が脆弱になり孔食状に摩耗が進み耐
摩耗性も低下するのでフェライト量40〜70チでも効
果があるが、その中でも最適量として50〜65チを限
定する。The ferrite volume fraction determines the precipitation hardenability of the alloy of the present invention.1
.. This has a large effect on wear resistance; if the amount of ferrite is small, sufficient precipitation hardening ability cannot be obtained, resulting in insufficient wear resistance, and if there is a large amount of ferrite, precipitation hardening occurs and the ferrite becomes brittle. At the same time, the relationship between the matrix and the precipitation becomes weak, wear progresses in the form of pitting corrosion, and wear resistance decreases, so a ferrite amount of 40 to 70 inches is effective, but the optimum amount is limited to 50 to 65 inches.
次に本発明の実施例を比較例と共にあげ2本発明合金の
特徴について詳述する。第1表は。Next, examples of the present invention will be presented along with comparative examples, and the characteristics of the alloy of the present invention will be described in detail. Table 1 is.
実施例としてあげた本発明合金と比較例としてあげた従
来合金と参考合金の組成と、フェライト体積率の測定結
果及び熱処理条件を示し、第2表は第1表の合金につい
ての硬さ、靭性及びPH3〜4.O4−1500ppm
、 F −500ppm。Table 2 shows the compositions, measurement results of ferrite volume fraction, and heat treatment conditions of the inventive alloy given as an example, the conventional alloy given as a comparative example, and the reference alloy. Table 2 shows the hardness and toughness of the alloys in Table 1. and PH3-4. O4-1500ppm
, F-500ppm.
フライアッシー05チ、珪砂40 wt%の硫酸性雰囲
気下に於けるスラリー循環回転式摩耗試験の結果を示す
。第1表の参考合金1〜5は本発明に近い合金であるが
フェライト量が限定範囲外のもので、第2表及び第1図
に示すように。The results of a slurry circulation rotary wear test in a sulfuric acid atmosphere using a 05-inch fly assembly and 40 wt% silica sand are shown. Reference alloys 1 to 5 in Table 1 are alloys close to the present invention, but the amount of ferrite is outside the limited range, as shown in Table 2 and FIG.
フェライト量が多い程、析出硬化能が大きく。The greater the amount of ferrite, the greater the precipitation hardening ability.
硬さは、フェライト含有量の増加に従って、はぼ直線的
に増加するが腐食環境下に於ける耐摩耗性は硬さと比例
せず、フェライト量50〜65チの範囲が最も耐摩耗性
が優れている。Hardness increases almost linearly as the ferrite content increases, but wear resistance in a corrosive environment is not proportional to hardness, and the wear resistance is the best in the range of 50 to 65 inches of ferrite. ing.
また、参考合金6,7は本発明合金との比較に於いて第
2図に示すように、 Ou含有量による第 、 2
表
摩耗試験条件:液組成、 PH3−4,Ct−1500
ppm、F−500ppmフライアッシ二〇5弧珪砂4
0w1%、(30〜50μ)馬連: 5m/’sec
テスト時間4008r
析出硬化能と耐摩耗性の関係を示すもので、析出硬化性
は、殆んどCu量の増加と共に大きくなっているが、耐
摩耗性はあまり高硬度になると靭性が低下することと塊
状の0u−rich相により孔食状に摩耗が進行するた
め耐摩耗性向上の顕著な範囲のCu量としては2〜5%
である。In addition, in comparison with the alloys of the present invention, Reference Alloys 6 and 7 have the following differences depending on the O content, as shown in FIG.
Surface wear test conditions: Liquid composition, PH3-4, Ct-1500
ppm, F-500ppm fly ash 205 arc silica sand 4
0w1%, (30-50μ) Horse Ren: 5m/'sec Test time 4008r This shows the relationship between precipitation hardenability and wear resistance, and precipitation hardenability mostly increases as the amount of Cu increases, but Regarding wear resistance, if the hardness is too high, the toughness will decrease and wear will progress like pitting corrosion due to the blocky 0u-rich phase, so the amount of Cu within the range where the wear resistance is significantly improved is 2 to 5%.
It is.
また第3図は本発明合金の析出硬化条件を決定するだめ
に実施したもので本発明合金の析出硬化能は、450〜
550℃間で最も顕著に硬化するのに対し、従来合金2
. 3 (SC!811)は600〜700℃の加熱に
よってフェライトが/グI相化し硬化する。しかし第2
表に示すように従来合金の耐摩耗性は、ングl相化によ
りヌ
脆化することと、/グl相が選択的に侵食され項中の耐
摩耗性は改善されない。In addition, Fig. 3 was conducted to determine the precipitation hardening conditions for the alloy of the present invention, and the precipitation hardening ability of the alloy of the present invention was 450~
It hardens most noticeably at 550°C, whereas conventional alloy 2
.. 3 (SC!811) is heated to 600 to 700°C, and the ferrite turns into I phase and hardens. But the second
As shown in the table, the wear resistance of conventional alloys is not improved due to the embrittlement caused by the formation of the N/G phase and the selective erosion of the /G phase.
以上記述したように本発明の耐食耐摩耗鋳鋼はオーステ
ナイトとフェライトの2相組織からなりフェライト量を
50〜65チにコノトロールしOuによる析出硬化を起
させることによって酸性腐食環境下で耐摩耗性の優れた
合金で、ポン
〃プ類、他本発明合金の特性を必要とする鋳造部材に広
く使用されるものである。As described above, the corrosion-resistant and wear-resistant cast steel of the present invention has a two-phase structure of austenite and ferrite, and by controlling the amount of ferrite to 50 to 65 inches and causing precipitation hardening by O, it has excellent wear resistance in an acidic corrosion environment. It is an excellent alloy and is widely used in pumps and other cast members that require the characteristics of the alloy of the present invention.
第1図は本発明の特徴を示す、フェライト量と酸性環境
下のスラリ摩耗量及び析出硬化能を示す線図で、第2図
は本発明の特徴元素である理条件と硬さの関係を示す図
である。Figure 1 is a diagram showing the characteristics of the present invention, which is a diagram showing the amount of ferrite, the amount of slurry wear in an acidic environment, and the precipitation hardening ability, and Figure 2 is a diagram showing the relationship between the physical conditions and hardness, which are the characteristic elements of the present invention. FIG.
Claims (1)
n0.5・〜1、5チ、0r22〜28%、Ni6〜1
jチ、 Mo1.5〜3.596. Cu2. o〜5
0チ、残部Ft及び不純物から″なり、かつフェライト
の体積率が50〜6゛5耐・貴重摩耗鋳鋼。0, 0.1% or less, Si0.5-1.5%, M
n0.5-1, 5chi, 0r22-28%, Ni6-1
jchi, Mo1.5-3.596. Cu2. o~5
0%, the remainder Ft and impurities, and the volume fraction of ferrite is 50~6゛5 resistant and valuable wear cast steel.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP9934181A JPS581062A (en) | 1981-06-26 | 1981-06-26 | Corrosion- and abrasion-resistant cast steel |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP9934181A JPS581062A (en) | 1981-06-26 | 1981-06-26 | Corrosion- and abrasion-resistant cast steel |
Publications (1)
Publication Number | Publication Date |
---|---|
JPS581062A true JPS581062A (en) | 1983-01-06 |
Family
ID=14244912
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP9934181A Pending JPS581062A (en) | 1981-06-26 | 1981-06-26 | Corrosion- and abrasion-resistant cast steel |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPS581062A (en) |
Cited By (5)
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CN102978531A (en) * | 2012-11-09 | 2013-03-20 | 宁波嘉达精密铸造有限公司 | Excavator bucket tooth and preparation method thereof |
CN103484772A (en) * | 2013-09-05 | 2014-01-01 | 宁波嘉达精密铸造有限公司 | Excavator tooth holder and preparation method thereof |
CN103498109A (en) * | 2013-09-05 | 2014-01-08 | 宁波嘉达精密铸造有限公司 | Excavator bucket tooth and preparation method thereof |
WO2018043214A1 (en) * | 2016-09-02 | 2018-03-08 | Jfeスチール株式会社 | Duplex stainless steel and method for manufacturing same |
WO2019098233A1 (en) * | 2017-11-15 | 2019-05-23 | 日本製鉄株式会社 | Two-phase stainless steel and method for manufacturing two-phase stainless steel |
-
1981
- 1981-06-26 JP JP9934181A patent/JPS581062A/en active Pending
Cited By (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN102978531A (en) * | 2012-11-09 | 2013-03-20 | 宁波嘉达精密铸造有限公司 | Excavator bucket tooth and preparation method thereof |
CN103484772A (en) * | 2013-09-05 | 2014-01-01 | 宁波嘉达精密铸造有限公司 | Excavator tooth holder and preparation method thereof |
CN103498109A (en) * | 2013-09-05 | 2014-01-08 | 宁波嘉达精密铸造有限公司 | Excavator bucket tooth and preparation method thereof |
CN103498109B (en) * | 2013-09-05 | 2015-07-15 | 宁波嘉达精密铸造有限公司 | Excavator bucket tooth and preparation method thereof |
WO2018043214A1 (en) * | 2016-09-02 | 2018-03-08 | Jfeスチール株式会社 | Duplex stainless steel and method for manufacturing same |
JP6358411B1 (en) * | 2016-09-02 | 2018-07-18 | Jfeスチール株式会社 | Duplex stainless steel and manufacturing method thereof |
RU2698235C1 (en) * | 2016-09-02 | 2019-08-23 | ДжФЕ СТИЛ КОРПОРЕЙШН | Two-phase stainless steel and its manufacturing method |
WO2019098233A1 (en) * | 2017-11-15 | 2019-05-23 | 日本製鉄株式会社 | Two-phase stainless steel and method for manufacturing two-phase stainless steel |
JPWO2019098233A1 (en) * | 2017-11-15 | 2020-11-19 | 日本製鉄株式会社 | Duplex Stainless Steel and Duplex Stainless Steel Manufacturing Methods |
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