JP2601392B2 - Welding material for hardfacing on cast iron - Google Patents
Welding material for hardfacing on cast ironInfo
- Publication number
- JP2601392B2 JP2601392B2 JP4216827A JP21682792A JP2601392B2 JP 2601392 B2 JP2601392 B2 JP 2601392B2 JP 4216827 A JP4216827 A JP 4216827A JP 21682792 A JP21682792 A JP 21682792A JP 2601392 B2 JP2601392 B2 JP 2601392B2
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- welding
- hardness
- temperature
- deposited metal
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Description
【０００１】[0001]
【産業上の利用分野】本発明は、鋳鉄母材への硬化肉盛
り用として用いられる、被覆アーク溶接棒、溶接ワイ
ヤ、および溶接用粉末等の溶接材料に関し、更に詳しく
は、アルミ、鋼板等の金属性薄板材等をプレス加工する
プレス金型をはじめとする冷間プレス金型等の形状が複
雑で溶接後における機械加工性と硬さとが必要とされる
分野に利用される溶接材料に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a welding material such as a coated arc welding rod, a welding wire, and a powder for welding used for hardfacing on a cast iron base material. Related to welding materials used in fields where the shape of cold press dies, including press dies for press working thin metallic sheets, etc., is complex and machinability and hardness after welding are required Things.
【０００２】[0002]
【従来の技術】例えば、アルミ、鋼板等の金属製薄板ロ
ール材から、一定長のブランク素材を切り取る場合のト
リミング金型や、このブランク素材をドロー金型で絞り
成形した後、周辺部の不要部を切除するためのトリミン
グ金型等を製造する方法として、所定の形状に鋳造した
金型素材に刃材としての溶接材料を硬化肉盛りし、この
肉盛り部分から刃を削り出す方法がある。2. Description of the Related Art For example, a trimming die for cutting a blank material of a certain length from a thin roll of metal such as aluminum or a steel plate, and drawing and drawing of this blank material with a draw mold, the peripheral portion becomes unnecessary. As a method of manufacturing a trimming mold or the like for cutting off a portion, there is a method in which a welding material as a blade material is hardened and overlaid on a mold material cast into a predetermined shape, and a blade is cut out from the overlaid portion. .
【０００３】前記の場合に使用される硬化肉盛り材料
は、肉盛りする製品の用途により選定され、従来では溶
着金属の合金含有量および硬さにより、ＪＩＳ Ｚ３２
５１やＡＷＳ Ａ５．１３等に多くの種類が規定され、
また、これ以外にも特別な用途に応じて合金成分組成を
工夫した溶接材料が市販されている。[0003] The hardfacing material used in the above case is selected according to the use of the product to be built, and conventionally, JIS Z32 is used depending on the alloy content and hardness of the deposited metal.
51 and AWS A5.13, etc.
In addition, other welding materials having alloy component compositions devised according to special applications are commercially available.
【０００４】上記のような硬化肉盛り用溶接材料の硬化
は、加工硬化による硬化、時効、析出硬化熱処理による
硬化、およびフレーム、高周波による焼き入れ硬化等が
あるが、通常の場合は溶接のままで硬化して所定の硬さ
となる。したがって、前記のようなトリミング金型等に
おいて、硬化肉盛り溶接を行ない、その後、超硬、セラ
ミックス系あるいは高速度鋼刃等で切削加工して刃を削
り出すような場合に、切削できる限界が溶着金属の硬さ
により生じてくる。特にフライス盤等による断続切削で
は、刃物の種類が限定され、切削加工の容易な硬さは通
常ＨＲＣ４５までである。そこで、ＨＲＣ４５以上の硬
さが必要な用途の場合には、焼きなましにより溶着金属
の硬さを下げて機械加工した後に焼入れにより硬さを上
げるか、または研削盤により研磨加工を行なわなければ
ならない。[0004] The hardening of the above-mentioned hardened overlay welding material includes hardening by work hardening, aging, hardening by precipitation hardening heat treatment, quenching hardening by a frame and high frequency, and the like. And hardens to a predetermined hardness. Therefore, in the case of the above-described trimming mold or the like, when hardfacing welding is performed, and thereafter, when the blade is cut out by cutting with a carbide, ceramics or high-speed steel blade or the like, the cutting limit is limited. It is caused by the hardness of the deposited metal. In particular, in intermittent cutting with a milling machine or the like, the type of cutting tool is limited, and the hardness for easy cutting is usually up to HRC45. Therefore, in applications requiring a hardness of HRC 45 or more, it is necessary to reduce the hardness of the deposited metal by annealing and then increase the hardness by quenching, or to perform polishing by a grinder.
【０００５】しかしながら、前者の焼きなましにより溶
着金属の硬さを下げて加工した後、焼き入れする方法の
場合は、高温加熱と冷却により歪が発生するために、仕
上げ代を残して切削加工し、最後に研削仕上げを行なう
必要があり、工程数が多く、高コストで、しかも長い工
期を必要とする。また、後者の研削盤により研磨加工す
る方法では、加工物の形状的制約とともに、やはり高コ
ストで、しかも長い工期が必要である。[0005] However, in the former method, the hardness of the deposited metal is reduced by annealing, followed by quenching, in which distortion occurs due to high-temperature heating and cooling. Finally, it is necessary to perform a grinding finish, which requires a large number of steps, is expensive, and requires a long construction period. In addition, in the latter method of polishing using a grinder, the cost is also high and a long construction period is required in addition to the restriction on the shape of the workpiece.
【０００６】更に、肉盛りする母材が鋳鉄の場合には、
その中に多量に含まれる炭素の影響を受け肉盛りした溶
着金属の硬さが上昇して靭性が低下し割れが発生する。
そのため第一層目にニッケル、鉄ニッケル等の下盛りを
行い防止しているが、このニッケルによる溶着金属の硬
さ低下のため、多層肉盛りが必要となる。Further, when the base material to be built is cast iron,
Under the influence of a large amount of carbon contained therein, the hardness of the deposited weld metal increases, the toughness decreases, and cracks occur.
For this reason, nickel, iron nickel, or the like is provided on the first layer to prevent the metal from being plated. However, since the hardness of the deposited metal is reduced by the nickel, a multilayer build-up is required.
【０００７】[0007]
【発明が解決しようとする課題】上記のように、従来の
硬化肉盛り用溶接材料においては、ＨＲＣ４５以上の硬
さが必要な場合には、機械加工性、高温加熱や冷却とい
った熱処理による歪、加工工程の煩雑さ、更に、母材が
鋳鉄の場合には炭素の影響による靭性の低下等の多くの
問題があった。本発明は上記の点に鑑み、鋳鉄母材への
硬化肉盛り用溶接材料として、直接肉盛りでき、良好な
機械加工性を有し、かつ簡単な処理でしかも歪等の発生
もなくＨＲＣ４５以上の硬さにまで硬化しうる肉盛り用
溶接材料を提供せんとするものである。As described above, in the conventional hardfacing welding material, when a hardness of HRC 45 or more is required, the workability, distortion due to heat treatment such as high temperature heating and cooling, There are many problems, such as the complexity of the processing steps, and the reduction in toughness due to the influence of carbon when the base material is cast iron. In view of the above points, the present invention can be directly welded as a welding material for hardfacing to a cast iron base material, has good machinability, and has a simple treatment and does not generate distortion or the like, and has an HRC of 45 or more. The purpose of the present invention is to provide a build-up welding material that can be hardened to a hardness equal to or less.
【０００８】[0008]
【課題を解決するための手段】本発明は、上記の目的を
達成するために、鋳鉄材への硬化肉盛り用溶接材料とし
て、溶着金属の基本成分組成がＣ０．５０〜１．５０
％、Ｓｉ０．２０〜２．００％、Ｍｎ０．３０〜６．０
０％、Ｃｒ０．３０〜１０．００％、Ｃｏ０．３０〜１
０．００％、残部Ｆｅおよび不可避の不純物であり、か
つマルテンサイト変態開始温度が１５０℃以下であっ
て、溶着金属の硬さが溶接したままではＨＲＣ４５以
下、溶接後０℃以下の過冷処理でＨＲＣ４５以上になる
溶接材料；溶着金属の基本成分組成が、前記溶接材料の
基本成分組成に更にＶ、Ｎｉ、Ｍｏ、Ｗ、Ａｌ、Ｃｕか
ら選んだ１種または２種以上を含むものであり、かつマ
ルテンサイト変態開始温度が１５０℃以下であって、溶
着金属の硬さが溶接したままではＨＲＣ４５以下溶接後
０℃以下の過冷処理でＨＲＣ４５以上になる溶接材料を
提供せんとするものである。上記の場合に、溶接材料と
は被覆アーク溶接棒、溶接ワイヤ、および溶接用粉末の
いずれをも含むものとする。According to the present invention, in order to achieve the above object, as a welding material for hardfacing to a cast iron material, the basic composition of the deposited metal is C0.50 to 1.50.
%, Si 0.20 to 2.00%, Mn 0.30 to 6.0
0%, Cr 0.30-10.00%, Co 0.30-1
0.00%, and the balance Fe and inevitable impurities, and the martensitic transformation start temperature Tsu der 0.99 ° C. or less
The hardness of the weld metal is HRC45
Below, a welding material which becomes HRC 45 or more by supercooling treatment of 0 ° C. or less after welding; the basic component composition of the deposited metal is further selected from V, Ni, Mo, W, Al, and Cu in addition to the basic component composition of the welding material. are those containing one or two or more, and the martensite transformation start temperature I der 0.99 ° C. or less, soluble
HRC45 or less after welding if the hardness of the deposited metal remains welded
The purpose of the present invention is to provide a welding material having an HRC of 45 or more by a supercooling treatment at 0 ° C. or less . In the above case, the welding material includes any of the covered arc welding rod, the welding wire, and the welding powder.
【０００９】また、上記の場合、マルテンサイト変態開
始温度（以下、「Ｍｓ温度」という。）とは下式により
計算した値をいう。尚、式中、各成分の値は％である。In the above case, the martensite transformation start temperature (hereinafter, referred to as “Ms temperature”) refers to a value calculated by the following equation. In the formula, the value of each component is%.
【００１０】Ｍs(℃)＝550−350×Ｃ−40×Ｍn−35×Ｖ
−20×Ｃr−17×Ｎi−10×Ｍo−5×Ｗ＋15×Ｃo＋30×
Ａl−10×Ｃu 尚、マルテンサイト変態終了温度（以下、「Ｍｆ温度」
という。）という場合は、下式により計算した値をい
う。Ms (° C.) = 550-350 × C-40 × Mn-35 × V
-20xCr-17xNi-10xMo-5xW + 15xCo + 30x
Al-10 × Cu Note that the martensitic transformation end temperature (hereinafter referred to as “Mf temperature”)
That. ) Means a value calculated by the following equation.
【００１１】Ｍf(℃)＝Ｍs−230 前記の場合に溶着金属の基本成分組成中の各成分の含有
量の範囲が限定される理由は以下のとおりである。先
ず、ＣはＭｓ温度、Ｍｆ温度の決定と、下の元素成分と
炭化物を作る最も有効な元素であって、このＣ量が０．
５０％未満ではＭｓ温度、Ｍｆ温度の調整で他の元素量
を多量に添加する必要が生じて不経済であり、また炭化
物量が不足して耐摩耗性が得られない。一方、このＣ量
が１．５０％を越えるとＭｓ温度、Ｍｆ温度が低下しす
ぎて他の元素を添加できず、そのために靭性のない溶着
金属となる。Mf (° C.) = Ms-230 The reason why the range of the content of each component in the basic component composition of the deposited metal is limited in the above case is as follows. First, C is the most effective element for determining the Ms temperature and Mf temperature and for forming carbides with the following elemental components.
If it is less than 50%, it is necessary to add a large amount of other elements by adjusting the Ms temperature and the Mf temperature, which is uneconomical, and the amount of carbides is insufficient and wear resistance cannot be obtained. On the other hand, if the C content exceeds 1.50%, the Ms temperature and the Mf temperature are too low, so that other elements cannot be added, resulting in a weld metal having no toughness.
【００１２】また、Ｓｉは脱酸効果と溶接中の溶着金属
の適度の粘性と流動性を上げ、作業性を向上させる元素
であり、このＳｉ量が０．２０％未満では前記のような
効果がなく、また、２．００％を越えて添加した場合に
は溶着金属の流れが良すぎ、盛り上がりが悪くなる。Further, Si is an element that improves the workability by increasing the deoxidizing effect and the appropriate viscosity and fluidity of the deposited metal during welding. If the amount of Si is less than 0.20%, the above-mentioned effect is obtained. If the addition exceeds 2.00%, the flow of the deposited metal is too good and the swelling becomes poor.
【００１３】Ｍｎ量の下限を０．３０％とした理由は、
このＭｎの量がこれ未満では脱酸不足でブローホールが
発生することによる。また、Ｍｎは比較的安価な元素
で、溶着金属の靭性向上や脱酸元素として、更には、Ｍ
ｓ温度、Ｍｆ温度を下げる効果として有効であるが、
６．００％を越えると溶接時のスケールが多くなり作業
性が低下するので、その上限は６．００％とした。The reason for setting the lower limit of the Mn content to 0.30% is as follows.
If the amount of Mn is less than this, blow holes are generated due to insufficient deoxidation. Further, Mn is a relatively inexpensive element, and is used as an element for improving the toughness of the deposited metal and as a deoxidizing element.
It is effective as an effect of lowering the s temperature and the Mf temperature.
If it exceeds 6.00%, the scale at the time of welding increases and the workability deteriorates. Therefore, the upper limit was set to 6.00%.
【００１４】また、ＣｒはＣとの親和力が強く、溶着金
属中で硬さの高い炭化物を形成して耐摩耗性を向上させ
る効果があるが、このＣｒ量が０．３０％未満ではその
効果がなく、また、１０．００％を越えると硬さが高く
なりすぎて耐割れ性、および靭性が低下する。Further, Cr has a strong affinity for C and has an effect of forming a carbide having a high hardness in the deposited metal to improve wear resistance. If the amount of Cr is less than 0.30%, the effect is reduced. If it exceeds 10.00%, the hardness becomes too high, and the crack resistance and the toughness decrease.
【００１５】更に、Ｃｏは炭化物の析出を遅らせ、溶接
のままでの硬さの上昇を抑制する効果があるが、このＣ
ｏ量が０．３０％未満ではそのような効果が得られず、
また、１０．００％を越えるとＭｓ温度、Ｍｆ温度が高
くなりすぎ、所要の硬さが得られず、またＣｏは高価な
ため不経済でもある。Further, Co has an effect of delaying the precipitation of carbides and suppressing an increase in hardness as it is welded.
If the amount of o is less than 0.30%, such an effect cannot be obtained,
On the other hand, if it exceeds 10.00%, the Ms temperature and the Mf temperature become too high, so that the required hardness cannot be obtained, and Co is expensive and uneconomical.
【００１６】尚、上記以外の元素の含有量としては、前
記の式により計算したＭｓ温度が＋１５０℃以下であれ
ばよい。また、ＴｉやＺｒといった元素は、Ｍｓ温度や
Ｍｆ温度には直接関係しないが、脱酸、作業性の改善等
といった効果があり、これらの金属元素を添加すること
もできる。更に、不純物については、本溶接材料の合金
作成に不可避なもの以外に、Ｍｓ温度が前記の＋１５０
℃以下になれば不純物の存在は特に問題とはならない。The content of the elements other than the above may be such that the Ms temperature calculated by the above equation is + 150 ° C. or less. Elements such as Ti and Zr are not directly related to the Ms temperature and the Mf temperature, but have effects such as deoxidation and improvement of workability, and these metal elements can be added. Further, regarding impurities, in addition to those inevitable in preparing an alloy of the present welding material, the Ms temperature is set to the above-mentioned +150.
If the temperature falls below ℃, the presence of impurities does not cause any particular problem.
【００１７】[0017]
【作用】上記のような本発明に係る溶接材料を用いて鋳
鉄母材に肉盛りすれば、例えば３層盛りの場合であれ
ば、第一層目および第二層目は鋳鉄母材中の炭素の巻き
込みによりＭｓ温度が常温以下となり、マンテルサイト
変態が完全に終了せず、溶着金属の組織は大部分が未変
態のオーステナイトとなる。このため、溶着金属の硬さ
は低く、軟らかく靭性のある金属となり、機械加工も容
易に行える。更に、同一溶接材料で肉盛りした第３層目
においては、溶着金属の特定の成分組成により、Ｍｓ温
度が＋１５０℃以下となるために、第一層目および第二
層目と同様に溶着金属の組織は未変態のオーステナイト
で占められ、溶接したままの溶着金属の硬さはＨＲＣ４
５以下となり、やはり機械加工を容易に行うことができ
る。そして、上記のように肉盛りした溶着金属を、機械
加工した後、ドライアイス、液体窒素、あるいは冷凍庫
等を用いて０℃以下に過冷することで、溶着金属のマン
テルサイト変態が開始しはじめ、残留オーステナイトが
マンテルサイトに変態し、硬さがＨＲＣ４５以上に上昇
して耐摩耗性のある溶着金属が得られる。また、このよ
うに過冷により硬度を上昇させるものであるから、従来
からの焼き入れする場合のように、金属が酸化したり、
あるいは高温加熱と冷却といった熱処理にともなう歪が
発生するといったこともなく、特別な仕上げ工程等も必
要としない。更には、肉盛りする母材が鋳鉄の場合で
も、その中に多量に含まれる炭素の影響により肉盛りし
た溶着金属の硬さが上昇して靭性が低下し割れが発生し
たりすることもなく、そのため従来のように第一層目に
ニッケル、鉄ニッケル等の下盛りを行う必要もなく、工
程数を大幅に低減することができる。When the above-mentioned welding material according to the present invention is used to build up a cast iron base material, for example, in the case of a three-layer build-up, the first and second layers are formed in the cast iron base material. The Ms temperature falls below room temperature due to the entrainment of carbon, the mantelsite transformation does not end completely, and the structure of the deposited metal is mostly untransformed austenite. For this reason, the hardness of the deposited metal is low, the metal becomes soft and tough, and machining can be easily performed. Further, in the third layer, which is built up with the same welding material, the Ms temperature becomes + 150 ° C. or less due to the specific composition of the deposited metal. Is composed of untransformed austenite, and the hardness of the as-welded deposited metal is HRC4
5 or less, so that machining can be easily performed. Then, after the weld metal deposited as described above is machined, it is supercooled to 0 ° C. or less using dry ice, liquid nitrogen, a freezer, or the like, so that the mantelsite transformation of the weld metal starts to start. Then, the retained austenite is transformed into mantelsite, and the hardness increases to HRC45 or more, so that a weld metal having wear resistance is obtained. In addition, since the hardness is increased by supercooling in this way, as in the case of conventional quenching, metal is oxidized,
Alternatively, there is no occurrence of distortion due to heat treatment such as high-temperature heating and cooling, and no special finishing step is required. Furthermore, even when the base material to be clad is cast iron, the hardness of the deposited metal that has been clad is increased due to the effect of carbon contained in the cast iron, and the toughness is reduced and cracks are not generated. Therefore, unlike the related art, it is not necessary to perform the underlaying of nickel, iron nickel, or the like on the first layer, and the number of steps can be greatly reduced.
【００１８】（実験）下記表１は、各成分の比率を変化
させた被覆アーク溶接棒の成分組成であり、表２に、表
１の溶接棒で普通鋳鉄（ＦＣ２５）上に溶接ビードを置
き、第一層目、第二層目、第三層目のそれぞれの溶着金
属についてＭｓ温度、Ｍｆ温度を調べた結果を示した。
また、表３には、前記溶接棒のブロホールを含む溶接作
業性、割れの有無、加工の難易、溶接のままの溶着金属
の硬さ、過冷処理後の溶着金属の硬さおよび硬化後の摩
耗減量を調べた結果を示した。尚、Ｎｏ．１〜１９の試
料については−７６℃（ドライアイス）で過冷処理を行
い、一方、Ｎｏ．２０〜２６の試料については−１９６
℃（液体窒素）で過冷処理を行なった。また、Ｎｏ．２
０〜２６の試料を−７６℃で過冷処理した場合の硬度と
摩耗減量を（ ）内に示した。(Experiment) Table 1 below shows the component composition of the coated arc welding rod in which the ratio of each component was changed. Table 2 shows a welding bead placed on ordinary cast iron (FC25) with the welding rod shown in Table 1. The results of examining the Ms temperature and Mf temperature of the first, second, and third layers of the deposited metal are shown.
Table 3 shows the welding workability of the welding rod including the blowhole, the presence or absence of cracks, the difficulty of processing, the hardness of the weld metal as it is welded, the hardness of the weld metal after supercooling and the hardness after the hardening. The results of examining wear loss are shown. In addition, No. The samples of Nos. 1 to 19 were supercooled at -76 ° C. (dry ice). -196 for samples 20-26
A supercooling treatment was performed at ℃ (liquid nitrogen). In addition, No. 2
The hardness and abrasion loss when the samples 0 to 26 were supercooled at -76 ° C are shown in parentheses.
【００１９】[0019]
【表１】 [Table 1]
【００２０】[0020]
【表２】 [Table 2]
【００２１】[0021]
【表３】 [Table 3]
【００２２】また、Ｍｓ温度を前出の式により求め、図
１にこのＭｓ温度と溶接したままの溶着金属の硬さおよ
び過冷処理後の溶着金属の硬さとの関係を示した。Further, the Ms temperature was determined by the above equation, and FIG. 1 shows the relationship between the Ms temperature and the hardness of the weld metal as welded and the hardness of the weld metal after the supercooling treatment.
【００２３】尚、摩耗減量については、図２に示すよう
に、２枚の試験片で１０kg／cm2の圧力で超硬板を挾み
込み、１分間に２０往復する速度で５万回摺動したとき
の試験前と試験後の重量差を測定した。As shown in FIG. 2, the wear loss was measured by sandwiching a cemented carbide plate between two test pieces at a pressure of 10 kg / cm 2 and sliding 50,000 times at a speed of 20 reciprocations per minute. The difference in weight before and after the test when moving was measured.
【００２４】上記の実験結果より、Ｍｓ温度が＋１５０
℃より高くなれば、溶着金属の硬さはＨＲＣ４５よりも
高くなり（Ｎｏ．２、９、１０、１２、１５）、また、
ドライアイスによる過冷処理ではＭｓ温度が０℃よりも
低くなると硬度を充分に上げられなくなるが（Ｎｏ．
４、１４）、液体窒素による過冷処理を行えば硬度を充
分に上げられることがわかる（Ｎｏ．２３）。従って、
Ｍｓ温度が＋１５０℃以下で、かつ溶着金属の成分組成
が上記した本発明の範囲内であれば、溶接のままでＨＲ
Ｃ４５以下で、かつ過冷処理後の硬さが４５以上になる
ことが判明した（Ｎｏ．５、７、１１、１８〜２６）。
また、供試溶接棒のＮｏ．１８、１９は、Ｍｓ温度およ
びＭｆ温度を調節する他の元素を添加し、またはＣｒ、
Ｍｎと置換した被覆アーク溶接棒であるが、硬さ、耐摩
耗性ともに同様の結果であることもわかる。According to the above experimental results, the Ms temperature was +150
C., the hardness of the deposited metal is higher than HRC45 (Nos. 2, 9, 10, 12, 15), and
In the supercooling process using dry ice, if the Ms temperature is lower than 0 ° C., the hardness cannot be sufficiently increased (No.
4, 14), it is found that the hardness can be sufficiently increased by performing the supercooling treatment with liquid nitrogen (No. 23). Therefore,
If the Ms temperature is not higher than + 150 ° C. and the component composition of the deposited metal is within the range of the present invention, the HR can be as-welded
It was found that C45 or less and hardness after the supercooling treatment was 45 or more (Nos. 5, 7, 11, 18 to 26).
In addition, the test welding rod No. 18, 19 add other elements that control the Ms and Mf temperatures, or
Although the coated arc welding rod was replaced with Mn, it can be seen that the same results were obtained in both hardness and wear resistance.
【００２５】表４は、前記表１に示すＮｏ．５とほぼ同
じ成分組成の１．２mmのワイヤ（Ｎｏ．２７）と、６０
〜２００メッシュの粉末（Ｎｏ．２８）の溶着金属の成
分組成であり、表５は前記ワイヤおよび粉末を用いてＭ
ＩＧ溶接および粉体プラズマ溶接で普通鋳鉄（ＦＣ２
５）に溶接を行い、溶着金属の第一層目、第二層目及び
第三層目のＭｓ温度、およびＭｆ温度を調べた結果を示
し、更に表６は、これらの溶接のままの溶着金属の硬さ
とドライアイスによる過冷処理後の溶着金属の硬さ、並
びに摩耗減量、溶接作業性、割れの有無、および加工の
難易を調べた結果を示したものである。Table 4 shows No. 1 shown in Table 1 above. 1.2 mm wire (No. 27) having almost the same component composition as
Table 5 shows the composition of the deposited metal of powder (No. 28) having a mesh size of ~ 200 mesh.
Cast iron (FC2) by IG welding and powder plasma welding
5) shows the results of examining the Ms temperature and the Mf temperature of the first, second and third layers of the deposited metal by welding, and Table 6 shows the welding of these welds as they are. It shows the results of examining the hardness of the metal and the hardness of the deposited metal after supercooling treatment with dry ice, as well as the loss of wear, welding workability, the presence or absence of cracks, and the difficulty of working.
【００２６】[0026]
【表４】 [Table 4]
【００２７】[0027]
【表５】 [Table 5]
【００２８】[0028]
【表６】 [Table 6]
【００２９】これから明らかなように、ワイヤや粉末を
用いたＭＩＧ溶接や粉体プラズマ溶接の場合において
は、第一層目、第二層目はとけ込みの違いにより前記溶
接棒による被覆アーク溶接の場合とは硬さが多少異なる
ものの、第三層目のＭｓ温度が＋１５０℃以下であれ
ば、溶接方法にかかわらず、被覆アーク溶接と同様の結
果が得られる。As is apparent from the above, in the case of MIG welding or powder plasma welding using a wire or powder, the first layer and the second layer are not covered by the above-described welding rod due to the difference in melting. Although the hardness is slightly different from the case, if the Ms temperature of the third layer is + 150 ° C. or lower, the same result as in the covered arc welding can be obtained regardless of the welding method.
【００３０】[0030]
【実施例】表１に示したＮｏ．５の組成からなる被覆ア
ーク溶接棒を用い、図３に示すように普通鋳鉄（ＦＣ２
５）に手溶接で三層の肉盛り溶接を行った。また、図４
に示すように従来の方法で四層に肉盛り溶接を行い、前
記の場合と比較した。EXAMPLE No. 1 shown in Table 1 was used. 5 using a coated arc welding rod having a composition of
In 5), three-layer overlay welding was performed by manual welding. FIG.
As shown in the figure, the overlay welding was performed on the four layers by the conventional method, and compared with the above case.
【００３１】前記の場合の溶接条件は下記のとおりであ
る。The welding conditions in the above case are as follows.
【００３２】（本発明に係る溶接材料（Ｎｏ．５）を用
いた場合の溶接条件） 溶接棒径 ３．２ｍｍ 溶接電流 ７０〜８０Ａｍｐ 予熱、後熱 なし 溶接速度 ８〜１０cm／min （従来法の溶接条件） 第一層目の被覆アーク溶接棒の成分組成（％） （ＪＩＳ Ｚ３２５２ ＤＦＣＮｉＦｅ） Ｃ Ｓｉ Ｍｎ Ｐ Ｓ Ｎｉ Ｆｅ ０．９２ ０．４８ ０．３２ ０．０１１ ０．０１０ ５６．２５ 残 溶接棒径 ３．２mm 溶接電流 １２０Amp 予熱、後熱 なし 溶接速度 １０cm／min 第二〜四層目の被覆アーク溶接棒の成分組成（％） （硬化肉盛り用溶接棒） Ｃ Ｓｉ Ｍｎ Ｐ Ｓ Ｎｉ Ｆｅ ０．３５ ２．９０ ０．２９ ０．０１０ ０．０１３ ９．０１ 残 溶接棒径 ３．２mm 溶接電流 １２０Amp 予熱、後熱 なし 溶接速度 １０cm／min 上記のようにして溶接した本発明に係る溶接棒と従来の
溶接棒とにおける、溶接した後の溶接のままの溶着金属
の断面硬度および本発明に係る溶接棒のドライアイスに
よる過冷処理後の溶着金属の断面硬度を測定し、その結
果を図５に示した。尚、加工性について溶接のままでの
従来の溶接金属と本発明の溶接金属とを切削加工し、刃
物にかかる背分力、送り分力および垂直分力の三分力を
測定した。その結果を表７に示した。(Welding conditions when the welding material (No. 5) according to the present invention is used) Welding rod diameter 3.2 mm Welding current 70 to 80 Amp Preheating and postheating None Welding speed 8 to 10 cm / min (conventional method) Welding conditions) Component composition (%) of the first-layer coated arc welding rod (JIS Z3252 DFCNiFe) CSiMnPSNiFe0.92 0.48 0.32 0.011 0.010 56.25 Remaining welding Rod diameter 3.2mm Welding current 120Amp Preheating, post-heating None Welding speed 10cm / min Component composition (%) of second to fourth layer coated arc welding rod (welding rod for hardfacing) CSiMnPSNiFe 0.35 2.90 0.29 0.010 0.013 9.01 Remaining welding rod diameter 3.2mm Welding current 120Amp No preheating or afterheating None Welding speed 10cm / min According to the present invention welded as described above In the welding rod and the conventional welding rod, the sectional hardness of the as-welded weld metal after welding and the sectional hardness of the weld metal after supercooling treatment with dry ice of the welding rod according to the present invention were measured. Is shown in FIG. For the workability, the conventional weld metal as welded and the weld metal of the present invention were cut, and the back component, the feed component and the vertical component applied to the blade were measured. Table 7 shows the results.
【００３３】[0033]
【表７】 [Table 7]
【００３４】[0034]
【発明の効果】以上の結果から明らかなように、本発明
に係る溶接材料を用いて鋳鉄母材に対して硬化肉盛りを
行った場合には、従来の方法に比べて溶接のままでの溶
着金属の硬さが低いことから、溶接後の切削加工が容易
で従来に比べて切削抵抗が約２５％軽減でき、切削速度
の向上が可能であり、また、工具刃物の欠損が生じない
ため、工具費の削減が可能であるとともに、刃物を取り
替える必要がなくＮＣフライス等による無人自動切削加
工も可能となる。更には、加工後においてはドライアイ
ス、液体窒素、あるいは冷凍庫等を用いて過冷処理する
だけの簡単な処理で溶着金属の硬さを上げることがで
き、しかも、肉盛りする母材が鋳鉄の場合における炭素
の影響で溶着金属の硬さが上昇して靭性が低下して割れ
が発生したりすることがないことから、従来のようにニ
ッケル、鉄ニッケル等の下盛りの必要もなく、ニッケル
による溶着金属の硬さ低下防止のための多層肉盛りの必
要がない。更には、従来の焼き入れ処理のように高温加
熱、冷却等による歪の発生もなく、加工後に特別な仕上
げを必要とせず、工程数を削減することが可能となり、
コストの低減、納期の短縮化をも可能とするものであ
る。As is evident from the above results, when the hardfacing is performed on the cast iron base material using the welding material according to the present invention, the welding is performed as it is in comparison with the conventional method. Since the hardness of the deposited metal is low, cutting after welding is easy, cutting resistance can be reduced by about 25% compared to the conventional method, cutting speed can be improved, and there is no breakage of the tool blade. In addition, the tool cost can be reduced, and it is not necessary to replace the blade, and unattended automatic cutting using an NC milling machine or the like can be performed. Furthermore, after processing, the hardness of the deposited metal can be increased by a simple process of merely supercooling using dry ice, liquid nitrogen, or a freezer, and the base metal to be built up is cast iron. In this case, the hardness of the deposited metal does not increase due to the influence of carbon and the toughness does not decrease and cracking does not occur. There is no need for a multi-layer build-up to prevent a decrease in the hardness of the deposited metal due to the above. Furthermore, unlike the conventional quenching process, there is no generation of distortion due to high temperature heating, cooling, etc., no special finishing is required after processing, and the number of steps can be reduced,
It is also possible to reduce cost and delivery time.
【図１】 溶着金属のＭｓ温度と硬度との関係を示すグ
ラフFIG. 1 is a graph showing a relationship between Ms temperature and hardness of a deposited metal.
【図２】 摩耗試験方法の説明図FIG. 2 is an explanatory view of a wear test method.
【図３】 本発明に係る溶接棒を用いた硬化肉盛り溶接
の説明図FIG. 3 is an explanatory diagram of hardfacing welding using the welding rod according to the present invention.
【図４】 従来の溶接棒を用いた硬化肉盛り溶接の説明
図FIG. 4 is an explanatory view of hardfacing welding using a conventional welding rod.
【図５】 溶着金属の断面硬度を示すグラフFIG. 5 is a graph showing the cross-sectional hardness of a deposited metal;
───────────────────────────────────────────────────── フロントページの続き (72)発明者 田中 敬三 埼玉県狭山市新狭山１丁目10番地１ ホ ンダエンジニアリング株式会社内 (72)発明者 西川 昇 埼玉県狭山市新狭山１丁目10番地１ ホ ンダエンジニアリング株式会社内 (72)発明者 河瀬 剛毅 神奈川県横浜市戸塚区東俣野町1186番16 号 (72)発明者 渡辺 正巳 大阪府高槻市北大樋町36番地 (56)参考文献 特開 昭63−199092（ＪＰ，Ａ) 特開 平１−22497（ＪＰ，Ａ) 特開 昭64−18599（ＪＰ，Ａ) 蓮井淳ら著「現代溶接技術大系《第15 巻》」（昭和55年１月23日）、産報出版 株式会社、第27−33頁 ────────────────────────────────────────────────── ─── Continuing on the front page (72) Keizo Tanaka, Inventor 1-10-1, Shinsayama, Sayama City, Saitama Prefecture Inside Honda Engineering Co., Ltd. (72) Inventor Noboru Nishikawa 1-1-10, Shinsayama, Sayama City, Saitama Prefecture (72) Inventor: Takeki Kawase 1186-16, Higashimatano-cho, Totsuka-ku, Yokohama-shi, Kanagawa Prefecture (72) Inventor: Masami Watanabe 36, Kita-Ohi-cho, Takatsuki-shi, Osaka (56) References: JP-A-63- 199092 (JP, A) JP-A-1-22497 (JP, A) JP-A-64-18599 (JP, A) Atsushi Hasui et al., “Modern Welding Technology Dai-kei << Volume 15 >>” (Jan. 1980) 23), Sanpo Publishing Co., Ltd., pages 27-33
Claims (2)
〜１．５０％、Ｓｉ０．２０〜２．００％、Ｍｎ０．３
０〜６．００％、Ｃｒ０．３０〜１０．００％、Ｃｏ
０．３０〜１０．００％、残部Ｆｅおよび不可避の不純
物からなり、かつマルテンサイト変態開始温度が１５０
℃以下であって、溶着金属の硬さが溶接したままではＨ
ＲＣ４５以下、溶接後０℃以下の過冷処理でＨＲＣ４５
以上になる鋳鉄材への硬化肉盛り用溶接材料。The basic composition of the deposited metal is C0.50
-1.50%, Si 0.20-2.00%, Mn 0.3
0 to 6.00%, Cr 0.30 to 10.00%, Co
0.30 to 10.00%, the balance being Fe and unavoidable impurities, and the martensitic transformation onset temperature is 150
℃ I der less, H is remained hardness of the weld metal is welded
RC45 or less, HRC45 by supercooling treatment of 0 ° C or less after welding
Welding material for hardfacing to cast iron materials as described above .
載の溶接材料の基本成分組成に更にＶ、Ｎｉ、Ｍｏ、
Ｗ、Ａｌ、Ｃｕから選んだ１種または２種以上を含むも
のであり、かつマルテンサイト変態開始温度が１５０℃
以下であって、溶着金属の硬さが溶接したままではＨＲ
Ｃ４５以下、溶接後０℃以下の過冷処理でＨＲＣ４５以
上になる鋳鉄材への硬化肉盛り用溶接材料。2. The basic composition of the deposited metal according to claim 1.
In addition to V, Ni, Mo,
Including one or more selected from W, Al, and Cu
And the martensitic transformation onset temperature is 150 ° C
If the hardness of the deposited metal is as welded, HR
C45 or less, HRC45 or less by supercooling treatment at 0 ° C or less after welding
Welding material for hardfacing on cast iron material to be on top .
Priority Applications (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP4216827A JP2601392B2 (en) | 1991-12-12 | 1992-08-14 | Welding material for hardfacing on cast iron |
| US08/070,716 US5361968A (en) | 1992-08-14 | 1993-06-01 | Method of manufacturing metallic press die |
Applications Claiming Priority (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP35216591 | 1991-12-12 | ||
| JP3-352165 | 1991-12-12 | ||
| JP4216827A JP2601392B2 (en) | 1991-12-12 | 1992-08-14 | Welding material for hardfacing on cast iron |
| US08/070,716 US5361968A (en) | 1992-08-14 | 1993-06-01 | Method of manufacturing metallic press die |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0615481A JPH0615481A (en) | 1994-01-25 |
| JP2601392B2 true JP2601392B2 (en) | 1997-04-16 |
Family
ID=27329932
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP4216827A Expired - Lifetime JP2601392B2 (en) | 1991-12-12 | 1992-08-14 | Welding material for hardfacing on cast iron |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2601392B2 (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6375895B1 (en) * | 2000-06-14 | 2002-04-23 | Att Technology, Ltd. | Hardfacing alloy, methods, and products |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS63199092A (en) * | 1987-02-12 | 1988-08-17 | Kubota Ltd | Welded overlay roll for hot rolling |
-
1992
- 1992-08-14 JP JP4216827A patent/JP2601392B2/en not_active Expired - Lifetime
Non-Patent Citations (1)
| Title |
|---|
| 蓮井淳ら著「現代溶接技術大系《第１５巻》」（昭和５５年１月２３日）、産報出版株式会社、第２７−３３頁 |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0615481A (en) | 1994-01-25 |
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