JP2967436B2 - Blast furnace tuyere - Google Patents
Blast furnace tuyereInfo
- Publication number
- JP2967436B2 JP2967436B2 JP3153791A JP3153791A JP2967436B2 JP 2967436 B2 JP2967436 B2 JP 2967436B2 JP 3153791 A JP3153791 A JP 3153791A JP 3153791 A JP3153791 A JP 3153791A JP 2967436 B2 JP2967436 B2 JP 2967436B2
- Authority
- JP
- Japan
- Prior art keywords
- blast furnace
- furnace tuyere
- alloy
- alloy layer
- tuyere
- 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.)
- Expired - Fee Related
Links
Landscapes
- Blast Furnaces (AREA)
Description
【０００１】[0001]
【産業上の利用分野】本発明は、耐久性、耐摩耗性を向
上させた高炉羽口に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a blast furnace tuyere with improved durability and wear resistance.
【０００２】[0002]
【従来の技術】溶鉱炉の熱風吹き込みに使用される高炉
羽口は、一般に銅を母材とし、内部には冷却水を供給し
て水冷式となっているが、炉内に突き出た羽口の先端
が、炉内の溶銑、溶滓、炉内装入物に接触する等の過酷
な環境下にある。従って、該溶銑等の接触によって高炉
羽口が溶損し易く、これによって羽口冷却水の漏れに基
づく爆発事故が発生したりするので、従来からＮｉ基自
溶性合金の肉盛を施す手段が多く採用されてきた。2. Description of the Related Art A blast furnace tuyere used for blowing hot air into a blast furnace is generally water-cooled by using copper as a base material and supplying cooling water to the inside thereof. The tip is in a harsh environment, such as in contact with hot metal, slag, and furnace interior materials in the furnace. Therefore, the blast furnace tuyere is liable to be damaged by the contact of the hot metal or the like, which may cause an explosion accident due to the tuyere cooling water leakage. Has been adopted.
【０００３】[0003]
【発明が解決しようとする課題】しかしながら、上記Ni
基自溶性合金によって肉盛した高炉羽口において、該溶
銑、溶滓のアタックの他、炉内装入物による機械的摩耗
も加わって耐用寿命が短いという問題点があった。ま
た、一方において、特開昭５３−１３８９０５号に示す
ように、高炉羽口の銅母材表面を、自溶性合金層、サー
メット層、セラミック層で順次被覆することによって耐
熱衝撃性及び、高温耐摩耗性を向上させた高炉羽口も提
案されているが、比較的コストが高くなり、大きな効果
が得られていないというのが現状である。本発明はかか
る事情に鑑みてなされたもので、過酷の条件の下にも従
来より比較的長期の寿命が得られる高炉羽口を提供する
ことを目的とする。However, the above-mentioned Ni
In a blast furnace tuyere laid up with a base self-fluxing alloy, there is a problem that the service life is short due to the mechanical abrasion caused by the inside of the furnace in addition to the attack of the hot metal and slag. On the other hand, as shown in JP-A-53-138905, the surface of the copper base material of the blast furnace tuyere is coated with a self-fluxing alloy layer, a cermet layer, and a ceramic layer in order to provide thermal shock resistance and high temperature resistance. Blast furnace tuyeres with improved wear properties have been proposed, but at present the cost is relatively high and no significant effect has been obtained. The present invention has been made in view of the above circumstances, and an object of the present invention is to provide a blast furnace tuyere capable of obtaining a relatively long life under conventional severe conditions.
【０００４】[0004]
【課題を解決するための手段】上記目的に沿う請求項第
１項記載の高炉羽口は、銅からなり内部を水冷した高炉
羽口において、該高炉羽口の少なくとも先部の表面にＮ
ｉ−Ｍｏの金属間化合物を含むビッカース硬度４００以
上のＮｉ−Ｍｏ合金層を被覆し、しかも、前記表面のＮ
ｉ−Ｍｏ合金層の下部にＮｉ−Ｃｒ合金層が形成されて
いる。そして、請求項第２項記載の高炉羽口は、請求項
第１項記載の高炉羽口において、Ｎｉ−Ｍｏ合金層は、
Ｍｏを２５〜４５重量％、Ｃｒを１０〜２０重量％を含
んでいる。According to the first aspect of the present invention, there is provided a blast furnace tuyere made of copper, the inside of which is water-cooled.
A Ni—Mo alloy layer having a Vickers hardness of 400 or more containing an intermetallic compound of i-Mo is coated, and N
A Ni-Cr alloy layer is formed below the i-Mo alloy layer. The blast furnace tuyere according to claim 2 is the blast furnace tuyere according to claim 1, wherein the Ni-Mo alloy layer is
It contains 25 to 45% by weight of Mo and 10 to 20% by weight of Cr.
【０００５】[0005]
【作用】請求項第１項及び第２項記載の高炉羽口におい
ては、少なくとも高炉羽口の先部に被覆されるＮｉ−Ｍ
ｏ合金層がＮｉ−Ｍｏの金属間化合物に依存している。
従って、その組成は軟質なマトリックス内に硬質の金属
間化合物の層が分散した構造となるので、従来から使用
されているＮｉ−Ｃｒ合金よりも硬度の点において遥か
に優れており、肉盛溶接によって接合することによっ
て、サーメット等より遥かに母材に接合強度が大きい。
また、融点は従来例に係るＮｉ−Ｃｒ合金より低いが、
高炉使用中の被覆層の表面温度は３００〜４００℃と推
定されるので、被覆層が溶融されることはない。また、
硬度がＨＶ４００以上と大きいので耐摩耗性に優れ、溶
銑、溶滓、コークス等の物理的接触に対して損耗するこ
とが少ない。そして、Ｎｉ−Ｍｏ合金層は軟質のマトリ
ックスに硬質の金属間化合物を分散させて硬度を保持す
る構造となっているので、繰り返し熱衝撃を与えた場
合、他のサーメット、セラミックあるいは自溶性合金に
比較しても、亀裂、剥離が生じ難い。更には、Ｎｉ−Ｍ
ｏ合金層の下部にＮｉ−Ｃｒ合金層が形成されているの
で、母材との溶接性に優れ、作業性及び経済性が向上す
る。In the blast furnace tuyere according to the first and second aspects, at least the Ni-M coated on the tip of the blast furnace tuyere is provided.
The o-alloy layer depends on the Ni-Mo intermetallic compound.
Therefore, since the composition has a structure in which a layer of a hard intermetallic compound is dispersed in a soft matrix, the composition is far superior in hardness to a conventionally used Ni-Cr alloy. By joining with the base material, the joining strength to the base material is far greater than that of cermet or the like.
Although the melting point is lower than that of the conventional Ni-Cr alloy,
Since the surface temperature of the coating layer during use of the blast furnace is estimated to be 300 to 400 ° C., the coating layer is not melted. Also,
Since the hardness is as high as HV400 or more, it has excellent wear resistance and is hardly worn by physical contact with hot metal, slag, coke, and the like. And, since the Ni-Mo alloy layer has a structure in which a hard intermetallic compound is dispersed in a soft matrix to maintain the hardness, when repeatedly subjected to thermal shock, it is applied to other cermets, ceramics or self-fluxing alloys. Even in comparison, cracking and peeling hardly occur. Furthermore, Ni-M
Since the Ni-Cr alloy layer is formed below the o alloy layer, the weldability with the base material is excellent, and the workability and economy are improved.
【０００６】[0006]
【実施例】続いて、本発明を具体化した一実施例につい
て説明し、本発明の理解に供する。まず、本発明の一実
施例に係る高炉羽口が従来例に係る高炉羽口より優れた
特性を有することを証明する為実験を行ったので、まず
これについて説明する。図２に示すように、銅母材１０
の上にまずＮｉ−Ｃｒ合金層１１を３ｍｍ程度下盛した
後、表１に示すような組成のＮｉ−Ｍｏ合金、ＷＣ−Ｎ
ｉ合金、及びＮｉ−Ｃｒ合金を上層１２として３ｍｍ程
度肉盛溶接をした。Next, an embodiment of the present invention will be described to provide an understanding of the present invention. First, an experiment was conducted to prove that the blast furnace tuyere according to one embodiment of the present invention had better characteristics than the blast furnace tuyere according to the conventional example. First, this will be described. As shown in FIG.
First, a Ni-Cr alloy layer 11 was laid down by about 3 mm, and then a Ni-Mo alloy having the composition shown in Table 1 and WC-N
The i-alloy and the Ni-Cr alloy were used as the upper layer 12 and overlaid by about 3 mm.
【０００７】そして、肉盛後の表面亀裂の発生の観察
（表面亀裂という）、それぞれの素材の肉盛後の断面亀
裂状況の観察（断面状態という）、顕微鏡による肉盛部
の亀裂発生、溶け込み状況の観察（顕微鏡観察）、以下
に説明する熱サイクル試験、常温硬さ、８００℃程度の
高温硬さ、作業性等を比較したものを表２に示す。上記
熱サイクルは図３に示すように、３０分かけて８００℃
に加熱して２０分程保持した後、急冷し、これを５０回
繰り返すことによって行い、亀裂発生、亀裂進行度合、
剥離の有無を観察することによって行った。表２から、
Ｎｉ−Ｍｏ合金に比較して硬度の点ではＷＣ−Ｎｉ合金
が優れるが、繰り返し熱サイクルを加えると亀裂、剥離
が発生するので、長期の寿命を保ち得ないことが分か
る。特に、高炉羽口においては、内部に溶銑、溶滓が存
在し、これらが繰り返し触れることによって繰り返し熱
応力が発生すると考えられ、長期の寿命を保ち難いと解
される。[0007] Observation of the occurrence of surface cracks after build-up (referred to as surface cracks), observation of the state of cross-sectional cracks after build-up of each material (referred to as cross-sectional state), generation of cracks in the build-up portion using a microscope, penetration Table 2 shows a comparison of the observation of the situation (microscopic observation), the heat cycle test described below, the normal temperature hardness, the high temperature hardness of about 800 ° C., the workability, and the like. As shown in FIG. 3, the heat cycle is performed at 800 ° C. for 30 minutes.
After heating and holding for about 20 minutes, quenching is carried out by repeating this 50 times.
This was performed by observing the presence or absence of peeling. From Table 2,
It can be seen that the WC-Ni alloy is superior in hardness in comparison with the Ni-Mo alloy, but cannot be maintained for a long term because cracks and peeling occur when repeated thermal cycling is applied. In particular, in the tuyere of blast furnace, hot metal and slag exist inside, and it is considered that repeated contact with these causes repeated thermal stress, and it is understood that it is difficult to maintain a long life.
【０００８】一方、Ｎｉ−Ｍｏ合金の平均硬度はＷＣ−
Ｎｉ合金より劣るが、マトリックス内に散在する金属間
化合物はＨＶ１１００程度であり、更には、上記熱サイ
クルをかけても剥離現象は見られ無かったので、高炉羽
口の表面コーテング材料としては優れた性質を有するこ
とが分かる。On the other hand, the average hardness of the Ni-Mo alloy is WC-
Although it is inferior to the Ni alloy, the intermetallic compound scattered in the matrix is about HV1100, and furthermore, no delamination was observed even after the above thermal cycle, so that it was excellent as a surface coating material for the blast furnace tuyere. It can be seen that it has properties.
【０００９】そこで、図１に示すように、銅製の高炉羽
口１３の先部を上記Ｎｉ−Ｍｏ合金の線材を使用してＴ
ＩＧ肉盛溶接を行う。この場合、肉盛溶接されたＮｉ−
Ｍｏ合金１４の成分は表１の通りである。Therefore, as shown in FIG. 1, the tip of the copper blast furnace tuyere 13 is made of T
Perform IG overlay welding. In this case, the Ni-
Table 1 shows the components of the Mo alloy 14.
【００１０】[0010]
【表１】 [Table 1]
【表２】 [Table 2]
【表３】 [Table 3]
【００１１】表３には、該Ｎｉ−Ｍｏ合金と従来例に係
る高炉羽口の肉盛に使用していたＮｉ−Ｃｒ合金の物理
的性状を示すが、表２に示すように、Ｎｉ−Ｍｏ合金は
融点はやや低いが、硬度がＮｉ−Ｃｒ合金より著しく大
きくなっている。また、繰り返し熱衝撃に対しては極め
て強い。なお、上記肉盛されたＮｉ−Ｍｏ合金層は高炉
羽口が炉内に入る先部のみとし、肉盛厚さは約３mm程度
とする。Table 3 shows the physical properties of the Ni-Mo alloy and the Ni-Cr alloy used for overlaying the blast furnace tuyere according to the conventional example. The Mo alloy has a slightly lower melting point, but has a significantly higher hardness than the Ni-Cr alloy. It is extremely strong against repeated thermal shock. The overlaid Ni-Mo alloy layer is formed only at the tip where the blast furnace tuyere enters the furnace, and the overlaid thickness is about 3 mm.
【００１２】そして、上記Ｎｉ−Ｍｏ合金層を肉盛溶接
した高炉羽口１３を使用した結果、従来の同一厚みのＮ
ｉ−Ｃｒ合金層を肉盛溶接した高炉羽口に比較して、略
１．５倍程度の寿命を有していた。Then, as a result of using the blast furnace tuyere 13 in which the above-mentioned Ni-Mo alloy layer is overlaid and welded, a conventional N-Mo alloy layer having the same thickness is obtained.
The life was approximately 1.5 times as long as the blast furnace tuyere in which the i-Cr alloy layer was overlay-welded.
【００１３】上記高炉羽口１３の場合には銅からなる高
炉羽口に直接Ｎｉ−Ｍｏ合金を略３ｍｍ〜６ｍｍの厚み
で肉盛溶接したが、予め施工し易いＮｉ−Ｃｒ合金を下
盛した後、その表面にＮｉ−Ｍｏ合金を上盛することも
可能である。また、上記実施例においては、Ｎｉ−Ｍｏ
合金層の成分を限定して実施したが、Ｎｉ−Ｍｏの金属
間化合物を有し、ビッカース硬度が４００以上であれ
ば、ニッケル、モリブデン、クロム、珪素の成分比率を
変えて施工することも可能である。更には、上記実施例
は該Ｎｉ−Ｍｏ合金の溶接をＴＩＧ溶接によって行った
が、ＭＩＧ溶接であっても良く、また上記実施例は高炉
羽口の先部のみにＮｉ−Ｍｏ合金層を形成したが、高炉
羽口の中間部も合わせてあるいは高炉羽口の全体をＮｉ
−Ｍｏ合金層によって被覆する場合も本発明は適用され
る。In the case of the above-mentioned blast furnace tuyere 13, a Ni-Mo alloy was directly welded to the blast furnace tuyere made of copper with a thickness of approximately 3 mm to 6 mm, but a Ni-Cr alloy which is easy to perform in advance was prepared. Later, it is also possible to overlay a Ni-Mo alloy on the surface. In the above embodiment, Ni-Mo
Although the composition of the alloy layer was limited, it was possible to change the composition ratio of nickel, molybdenum, chromium, and silicon as long as it had an intermetallic compound of Ni-Mo and had a Vickers hardness of 400 or more. It is. Further, in the above embodiment, the Ni-Mo alloy was welded by TIG welding, but it may be MIG welding. In the above embodiment, the Ni-Mo alloy layer is formed only at the tip of the blast furnace tuyere. However, the middle of the blast furnace tuyere was also combined or the entire blast furnace tuyere was
The present invention is also applicable to the case of coating with a -Mo alloy layer.
【００１４】[0014]
【発明の効果】請求項第１項、第２項記載の高炉羽口
は、少なくとも高炉羽口の先部の表面がＮｉ−Ｍｏ合金
層によって被覆されているので、従来のＮｉ−Ｃｒ合金
によって被覆処理された高炉羽口より長期の寿命を得る
ことができる。また、サーメット、セラミック等の被覆
に比較して工事費用が安く、またコークスあるいは溶
銑、溶滓等の物理的あるいは熱衝撃があっても、剥離す
ることが少なく、高炉羽口事故を減少することができ
る。そして、Ｎｉ−Ｍｏ合金層の下部にＮｉ−Ｃｒ合金
層が形成されているので、母材との溶接性に優れ、作業
性及び経済性が向上する。According to the first and second aspects of the present invention, at least the surface of the tip of the blast furnace tuyere is covered with a Ni-Mo alloy layer. Longer life can be obtained than the coated blast furnace tuyere. In addition, the construction cost is lower than that of coating with cermet, ceramic, etc., and even if there is physical or thermal shock of coke, hot metal, slag, etc., there is little peeling and blast furnace tuyere accidents are reduced. Can be. And since the Ni-Cr alloy layer is formed under the Ni-Mo alloy layer, the weldability with the base material is excellent, and the workability and economy are improved.
【図１】本発明の一実施例に係る高炉羽口の部分断面図
である。FIG. 1 is a partial sectional view of a blast furnace tuyere according to one embodiment of the present invention.
【図２】本発明の作用、効果を確認する為に行った実験
に使用した試験片の側面図である。FIG. 2 is a side view of a test piece used in an experiment performed to confirm the operation and effect of the present invention.
【図３】熱サイクルの工程を示すグラフである。FIG. 3 is a graph showing steps of a thermal cycle.
１０ 銅母材 １１ Ｎｉ−Ｃｒ合金層 １２ 上層 １３ 高炉羽口 １４ Ｎｉ−Ｍｏ合金層 Reference Signs List 10 Copper base material 11 Ni-Cr alloy layer 12 Upper layer 13 Blast furnace tuyere 14 Ni-Mo alloy layer
Claims (2)
いて、該高炉羽口の少なくとも先部の表面にＮｉ−Ｍｏ
の金属間化合物を含むビッカース硬度４００以上のＮ１
−Ｍｏ合金層を被覆し、しかも、前記表面のＮｉ−Ｍｏ
合金層の下部にＮｉ−Ｃｒ合金層が形成されていること
を特徴とする高炉羽口。1. A blast furnace tuyere made of copper and the inside of which is water-cooled, Ni-Mo is applied to at least the front surface of the blast furnace tuyere.
N1 having a Vickers hardness of 400 or more containing an intermetallic compound of
-Mo alloy layer and Ni-Mo on the surface
A blast furnace tuyere characterized in that a Ni-Cr alloy layer is formed below the alloy layer.
重量％、Ｃｒを１０〜２０重量％を含む請求項第１項記
載の高炉羽口。2. The Ni—Mo alloy layer has a Mo content of 25 to 45.
The blast furnace tuyere according to claim 1, which contains 10 to 20% by weight of Cr and 10 to 20% by weight of Cr.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3153791A JP2967436B2 (en) | 1991-01-30 | 1991-01-30 | Blast furnace tuyere |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3153791A JP2967436B2 (en) | 1991-01-30 | 1991-01-30 | Blast furnace tuyere |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH04246113A JPH04246113A (en) | 1992-09-02 |
| JP2967436B2 true JP2967436B2 (en) | 1999-10-25 |
Family
ID=12333946
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP3153791A Expired - Fee Related JP2967436B2 (en) | 1991-01-30 | 1991-01-30 | Blast furnace tuyere |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2967436B2 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102660727A (en) * | 2012-04-10 | 2012-09-12 | 闽东宏宇冶金备件有限公司 | Multi-component alloy co-impregnated impregnant |
Families Citing this family (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102847933A (en) * | 2012-09-12 | 2013-01-02 | 江西重科机械有限公司 | High-temperature wear-resistant material adapted to lining of blast-furnace tuyere and preparation method of high-temperature wear-resistant material |
| CN104404186B (en) * | 2014-11-24 | 2016-08-24 | 武汉钢铁(集团)公司 | Strengthen function the manufacture method of functionally gradient material (FGM) in a kind of air port |
| JP7215010B2 (en) * | 2018-08-03 | 2023-01-31 | 日本製鉄株式会社 | Blast furnace tuyere and manufacturing method thereof |
| JP7260732B2 (en) * | 2018-08-03 | 2023-04-19 | 日本製鉄株式会社 | Blast furnace tuyere and manufacturing method thereof |
-
1991
- 1991-01-30 JP JP3153791A patent/JP2967436B2/en not_active Expired - Fee Related
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102660727A (en) * | 2012-04-10 | 2012-09-12 | 闽东宏宇冶金备件有限公司 | Multi-component alloy co-impregnated impregnant |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH04246113A (en) | 1992-09-02 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US8574686B2 (en) | Microwave brazing process for forming coatings | |
| US4003715A (en) | Copper-manganese-zinc brazing alloy | |
| CN104797728A (en) | Ni-cr-co-based alloy having high-temperature corrosion resistance properties, and poppet valve having surface modified with same | |
| Han et al. | Vacuum brazing of TZM alloy to ZrC particle reinforced W composite using Ti-28Ni eutectic brazing alloy | |
| JP2967436B2 (en) | Blast furnace tuyere | |
| JP4721185B2 (en) | Mold repair paste | |
| US4150818A (en) | Cooling element for a metallurgical furnace | |
| JP2578616B2 (en) | Solution treated heat-treated poppet valve and method for producing the same | |
| JP3644532B2 (en) | Ni-base heat-resistant alloy with excellent hot workability, weldability and carburization resistance | |
| JPH0872110A (en) | Component for injection molding machine, screw for injection molding machine, and production of the screw | |
| JP3576479B2 (en) | Water-cooled steel structure | |
| JPH1177375A (en) | Cobalt base alloy for cladding hot forging die by welding | |
| JP2793759B2 (en) | Cold water skirt for converter exhaust gas hood | |
| JPH086019Y2 (en) | Tuyere with excellent wear and peeling resistance at high temperatures | |
| JP4827047B2 (en) | Steel structure with corrosion resistance, wear resistance and heat crack resistance | |
| JPS5933181B2 (en) | Copper alloy for burner head | |
| JP2527229Y2 (en) | Blast furnace tuyere | |
| JP2002283030A (en) | Member for light alloy injection molding machine | |
| JPH06190588A (en) | Ni-base alloy for filling | |
| EP1380381B1 (en) | Nickel based filler metal for brazing | |
| JP3113234B2 (en) | Screw for injection molding machine and method of manufacturing the screw | |
| JP2597105B2 (en) | Copper member surface hardening method | |
| JPH08232058A (en) | Member for die casting and its production | |
| JPS62170466A (en) | Formation of thermally sprayed heat resistant film on copper alloy as base material | |
| JPS61186190A (en) | Composite filter rod for building up by welding |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| LAPS | Cancellation because of no payment of annual fees |