JPS61113713A - Manufacture of cast alloy for tool - Google Patents
Manufacture of cast alloy for toolInfo
- Publication number
- JPS61113713A JPS61113713A JP23513784A JP23513784A JPS61113713A JP S61113713 A JPS61113713 A JP S61113713A JP 23513784 A JP23513784 A JP 23513784A JP 23513784 A JP23513784 A JP 23513784A JP S61113713 A JPS61113713 A JP S61113713A
- Authority
- JP
- Japan
- Prior art keywords
- tool
- heat treatment
- seizure
- solidus
- carbide
- 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
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Articles (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
Description
【発明の詳細な説明】
発明の背景
ニー、熱間押出用ダイスなど、高温の被加工材との間の
厳しいすべり摩擦によって生ずる摩耗や焼付きが工具寿
命や製品品質を支配するような工具用鋳造合金の製造方
法に関するものである。[Detailed Description of the Invention] Background of the Invention For tools such as dies for hot extrusion, where wear and seizure caused by severe sliding friction with high-temperature workpieces dominate tool life and product quality. The present invention relates to a method for manufacturing a cast alloy.
（従来技術）
従来、ガイドシュー材には１．２％Ｃ−２５％Ｏｒ −
５％Ｎｉ系や１％Ｃ−５５％Ｃｒ −５５％Ｎｉ−Ｏｕ
−Ｍｏ −Ｗ系などの高合金浩鋼が鉤込みのま〜で使用
されていたが、被加工材が１１００〜１２５０Ｃの高温
であるうえに面圧が為く、工具−被加工材間で完全なす
べ夛摩擦を生ずるなど摩擦条件が非常に過酷であるため
に摩耗が著しく、工具寿命が短かい欠点があった。さら
にあるが、上記のような厳しい摩擦条件である故にガイ
ドシューと被加工材との間で焼付きが発生し易く、ガイ
ドシューマークと呼ばれる凹疵が被加工材表面に多数発
生し、大きな問題となっている。(Prior art) Conventionally, guide shoe material contains 1.2%C-25%Or-
5%Ni type or 1%C-55%Cr-55%Ni-Ou
High-alloy steels such as -Mo-W series have been used for hooking, but the workpiece is at a high temperature of 1100 to 1250C and surface pressure is generated between the tool and the workpiece. The friction conditions are very severe, such as complete sliding friction, resulting in significant wear and short tool life. Furthermore, due to the severe friction conditions mentioned above, seizure is likely to occur between the guide shoe and the workpiece, and many dents called guide shoe marks occur on the surface of the workpiece, which is a big problem. It becomes.
本発明は斯る問題に鑑み、熱間加工用合金工具鋼の成分
設計と熱処理との組合せＫよって、合金工具鋼を提供す
ることを目的とする工具用鋳造合金の製造方法に関する
ものである。In view of such problems, the present invention relates to a method for producing a casting alloy for tools, which aims to provide an alloy tool steel by combining the compositional design and heat treatment of the alloy tool steel for hot working.
（発明の概要及び詳細な説明）
本発明者らは工具用鋳造合金の耐摩耗性、耐焼付き性を
改善すべく、Ｉ？ｌＦＫ：炭化物性状に着目して研究を
行なってきた結果、粗大炭化物が数多く含有する鋼種な
と耐摩耗性、耐焼付き性が良好であるという知見を得、
このような観点からさらに研究を進めた結果、下記に示
すようなしても焼付きな生じないことを見り出した。本
発明は斯る知見に基きなされ九もので、その要旨とする
ところＢａａ、ａ〜２．５％、Ｓｉ３％以下、Ｍｎ３％
以下、Ｃｒ２０〜４０％、Ｎｉ２０〜５０％を含有し、
さらに必要に応じてＭｏ Ｏ，１〜５％、！０．１〜５
％、 Ｇｏ ０．１〜５％、Ｔｉ０．１〜５％、 Ｖ
Ｏ，１〜５％、 ｚｒ ０．ｔ〜５％のうちの１種又は
２種以上を含有し、残部Ｆ６ 及び不可避的不純物よ
υ成る高合金鋳鋼を固相線よシ２０Ｃ低い温度から固相
線より４ａＣ高い温度までの温度範囲にて１〜２０時間
加熱、保持する耐摩耗性、耐焼付き性良好な工具用鋳造
合金の製造方法である。(Summary and Detailed Description of the Invention) In order to improve the wear resistance and seizure resistance of a cast alloy for tools, the present inventors investigated I. IFK: As a result of conducting research focusing on carbide properties, we have found that steel types that contain a large number of coarse carbides have good wear resistance and seizure resistance.
As a result of further research from this point of view, it was discovered that even if the method shown below is used, image sticking does not occur. The present invention has been made based on this knowledge, and its gist is that Baa, a ~ 2.5%, Si 3% or less, Mn 3%
Contains 20-40% Cr and 20-50% Ni,
Furthermore, if necessary, add MoO, 1 to 5%! 0.1~5
%, Go 0.1-5%, Ti 0.1-5%, V
O, 1-5%, zr 0. High-alloy cast steel containing one or more of the following: F6 and unavoidable impurities in a temperature range from 20C below the solidus to 4aC above the solidus. This is a method for producing a cast alloy for tools with good wear resistance and seizure resistance, by heating and holding the alloy for 1 to 20 hours.
以下に、成分組成範囲及び熱処理条件を上記の通シ限定
した理由について説明する。The reason why the component composition range and heat treatment conditions are limited to the above-mentioned range will be explained below.
（ａ） 成分組成範囲の限定理由
ＧはＣｒ、Ｉｒｅ等と結合してＭ２３Ｃ６型およびＭ、
Ｃ３型炭化物を形成するが、上述の熱処理によってこれ
らの炭化物を凝集・粗大化せしめるためには鋳込みのま
まの状態で所望の炭化物量を確保することが必要である
。Ｃが０．８％未満では所望の炭化物量を確保できない
ために熱処理を施しても耐摩耗性、耐焼付き性を改善す
る効果が十分でなく、一方２．５％を越えて含有させる
と炭化物が過度に存在するために靭性が低下して割れが
発生することから、その含有量を０．８〜２．５％に限
定した。(a) Reason for limiting the component composition range G combines with Cr, Ire, etc. to form M23C6 type and M,
Although C3 type carbides are formed, in order to aggregate and coarsen these carbides by the above-mentioned heat treatment, it is necessary to secure a desired amount of carbides in the as-cast state. If C is less than 0.8%, the desired amount of carbides cannot be secured, so even if heat treatment is applied, the effect of improving wear resistance and seizure resistance will not be sufficient.On the other hand, if C is contained more than 2.5%, carbide Since the presence of an excessive amount of C reduces toughness and causes cracks, its content was limited to 0.8 to 2.5%.
Ｓｉ は脱酸調整および鋳造性改善のために有効であ
るが、過度に含有すると靭性な損なうため上限を３％と
した。Although Si is effective for adjusting deoxidation and improving castability, excessive Si content impairs toughness, so the upper limit was set at 3%.
Ｍｎ は脱酸作用な有するとともに高温強度を高め耐
摩耗性ン向上させる効果があるが、過度に含有すると靭
性を低下させるので上限ン３％とした。Mn has a deoxidizing effect and has the effect of increasing high-temperature strength and improving wear resistance, but if excessively contained, toughness decreases, so the upper limit was set at 3%.
Ｏｒ は基地に固溶して高温強度を高めるとともに上
記のようＫＯと結合して炭化物を形成することにより、
耐摩耗性、耐焼付き性の改善に寄与する。ｃｒ が２０
％未満ではその効果が十分に得られず、４０％を越えて
含有するとσ相の析出により脆化するので、２０〜４０
％に限定した。Or is dissolved in the matrix to increase high-temperature strength, and as described above, by combining with KO to form carbide,
Contributes to improving wear resistance and seizure resistance. cr is 20
If the content is less than 40%, the effect will not be sufficiently obtained, and if the content exceeds 40%, it will become brittle due to the precipitation of the σ phase.
%.
Ｎｉ は靭性および耐熱衝撃性を高める効果がめるが、
その含有量が２０％未満で紘所望の効果が得られず、ま
た５０％を越えて含有してもよシ一層の効果が望めない
ので、経済性をも考慮して２０〜５０％に限定した。Ni has the effect of increasing toughness and thermal shock resistance, but
If the content is less than 20%, the desired effect cannot be obtained, and even if it is more than 50%, no further effect can be expected. did.
Ｍ０．Ｗ、ＣｏｔＴｉ、ＶおよびＺｒは基地に固溶して
強度ン高めるとともにＣと結合して炭化物を形成し耐摩
耗性、耐焼付き性を向上させる作用があシ、含有量が多
ｉ程その効果も増すが、経済性をも考慮して各０．１〜
５％に限定した。M0. W, CotTi, V, and Zr solidly dissolve in the matrix to increase strength, and combine with C to form carbides to improve wear resistance and seizure resistance.The higher the content, the stronger the effect. However, considering economic efficiency, each value is 0.1~
It was limited to 5%.
（ｂ） 熱処理条件の限定理由
本発明の熱処理の特徴は液相から晶出した一次炭化物の
凝集・粗大化を目的としているので、通常の熱処理とは
異なシ非常に高い温度に加熱・保持することが必要であ
る。まず、加熱温度は固相線よりも２０Ｃ以上低いと後
述の保持時間範囲で炭化物の凝集・粗大化が十分に起こ
り得す、一方面相線よシも４０Ｃ以上高くすると被熱処
理材が部分的に溶融し始め、もとの形状を保ち得ないの
で、固相線よりも２０Ｃ下から固相線よりも４０Ｃ上ま
での温度範囲に限定する。(b) Reason for limiting heat treatment conditions The heat treatment of the present invention is characterized by the purpose of agglomerating and coarsening primary carbides crystallized from the liquid phase. It is necessary. First, if the heating temperature is 20C or more lower than the solidus line, agglomeration and coarsening of carbides may occur sufficiently within the holding time range described below.On the other hand, if the heating temperature is 40C or more higher than the solidus line, the material to be heat-treated may partially Since it begins to melt and cannot maintain its original shape, the temperature range is limited to 20C below the solidus line to 40C above the solidus line.
ここで固相線とは、熱分析曲線から得られる凝固終了温
度を意味する。成分系によって固相線温度は異なるが、
上記のごとき高Ｃ系合金鋼では１２５０〜１３５０ｃの
範囲であるから、実際の熱処理温度範囲は＋２３０−１
３９ｏＣである。Here, the solidus line means the solidification end temperature obtained from the thermal analysis curve. Although the solidus temperature varies depending on the component system,
Since the high C alloy steel mentioned above is in the range of 1250 to 1350c, the actual heat treatment temperature range is +230-1
It is 39oC.
保持時間は加熱温度とのかねあいでその長さを決定する
必要があるが、被熱処理材が溶融し始めない温度で炭化
物を凝集・粗大化せしめるためＫは最低１時間は必要で
あり、下限の温度で熱処理する場合にはさらに長時間の
保持が必要であるが、経済性を前置して上限を２０時間
とした。The holding time must be determined in consideration of the heating temperature, but in order to coagulate and coarsen the carbide at a temperature where the material to be heat treated does not begin to melt, K is required to be at least 1 hour. In the case of heat treatment at a higher temperature, it is necessary to hold the temperature for a longer time, but the upper limit was set at 20 hours in consideration of economic efficiency.
冷却速度は炭化物の凝集・粗大化には直接影響を及はさ
ないので特に限定するものではないが、炭化物量が多い
ほど耐摩耗性、耐焼付き性には有利であるから、高温に
おいて基地に固溶しているＣをもできる限シ炭化物とし
て析出せしめるべく、徐冷することか好ましい。上記熱
処理条件の限定範囲内でも特に作業性や経済性時間加熱
・保持し、６００Ｃ以下まで炉冷することか好ましい。The cooling rate is not particularly limited as it does not directly affect the agglomeration and coarsening of carbides, but the greater the amount of carbides, the better the wear resistance and seizure resistance. It is preferable to perform slow cooling in order to precipitate as much C as possible in solid solution as carbide. Even within the limited range of the heat treatment conditions described above, it is preferable to heat and hold the material for a time particularly in terms of workability and economy, and then to cool it in a furnace to 600C or less.
また、雰囲気は本熱処理の目的である炭化物の凝集・粗
大化に影響を及ぼさないので特に限定するものではなく
、通常は大気中でさしつかえない。Further, the atmosphere is not particularly limited as it does not affect the aggregation and coarsening of carbides, which is the purpose of the main heat treatment, and the atmosphere is usually suitable.
水元ＢＡは上記組成の高合金鋼ン熱処理し、凝集・粗大
化せしめた炭化物組織ヶ有することを特徴としており、
このような炭化物組織が耐摩耗性、耐焼付き性の向上べ
大きく寄与する熱処理による炭化物の組織変化の一例を
第１図に示す。Mizumoto BA is characterized by having a carbide structure that is agglomerated and coarsened through heat treatment of high alloy steel with the above composition.
FIG. 1 shows an example of a change in carbide structure due to heat treatment, in which such a carbide structure greatly contributes to improvements in wear resistance and seizure resistance.
第１図は０．９％Ｃ−５５％Ｏｒ −３５％Ｎｉ鋼の鋳
造組織ｔａｒと熱処理後の組織（ｂｌと比較顕微鏡写真
（ｘｓｏｏ）である。FIG. 1 shows a micrograph (xsoo) for comparison with the cast structure tar and the structure after heat treatment (bl) of 0.9%C-55%Or-35%Ni steel.
第１図（ＩＬ）の鋳造組織では炭化物量デンドライト状
の初晶オーステナイトの間隙に共晶状に存在しているが
、これ’４ｔ３ｏｏｃに５時間保持した後の第１図（ｂ
）の熱処理後の組織では炭化物が凝集・粗大化し、５〜
２０μｍの粒状炭化物−に変化していることがわかる。In the cast structure shown in Figure 1 (IL), the amount of carbides exists in a eutectic form in the gaps of dendrite-like primary austenite.
) In the structure after heat treatment, carbides aggregate and coarsen, and
It can be seen that it has changed to granular carbide with a diameter of 20 μm.
次に本発明の実施例を従来の鋳造合金と対比して示す。Next, examples of the present invention will be shown in comparison with conventional cast alloys.
下記第１表に本発明合金鋼と従来の工具鋼との成分組成
及び熱処理条件ン示す。Table 1 below shows the compositions and heat treatment conditions of the alloy steel of the present invention and conventional tool steel.
上記第１表に示す本発明工具用鋳造合金鋼及び従来合金
工具鋼と５ＴＢＡ ２４鋼及びＳ’ｌ’ＢＡ ２６鋼（
Ｇ５４６２、ボイラ熱交換器用合金鋼鋼管）との摩擦試
験を行ない、耐摩耗性、耐焼付き性を調査し、その結果
を第２表、第５表に示す。Cast alloy steel for tools of the present invention and conventional alloy tool steel shown in Table 1 above, 5TBA 24 steel and S'l'BA 26 steel (
Friction tests were conducted with G5462 (alloy steel tubes for boiler heat exchangers) to investigate wear resistance and seizure resistance, and the results are shown in Tables 2 and 5.
１）実験室的試験結果
第２図に示すような試験装置を用いて調査した結果を第
２表に示す。第２図において（１１は、工具用鋳造合金
に相当する試験片で６９、油圧シリンダによって往復運
動するホルダ（２）によって固定されている。一方（３
）は被加工材に相当する試験片であシ、モータによって
回転するホルダ（４）に固定され外周速度１ ｍ ／
Ｓで回転すると同時に高周波誘導によｆｉｌｏｏｏＣに
加熱保持されている。加圧力２００ｋｊＬｆ、５分間摩
擦した試験結果が第２表に示され、表中耐焼付き性は摩
擦試験後の試験片＠の表面状態を目視によ）判定した結
果を示し、○：焼付きが発生せず一様に摩耗した場合、
Δニ一様に摩耗しているが部分的に焼付きを生じて相手
材が付着している場合、×：焼付きを生じて摩擦面全面
に相手材が付着している場合を示す。また摩耗量は摩耗
痕の幅から算出し、摩耗体積で示した。全面に焼付きが
生じた場合には、相手材の付着のため正確な測定が不可
能なため、表からは除外したＯ
第２表
２）モデル穿孔ゝ昏会よる試験結果
次に、実験室的試験に供した試験材の中から数鋼種を選
び、モデル穿孔機用ガイドシューを作製して延伸試験を
行なった結果を第５表に示す。試験結果は直径４０φ、
肉厚７ｍ、長さ２００ｍの中空素管を長さ４００ｍに延
伸し、これを２０回繰）返した場合のものである。第３
表の耐焼付き性は第２表と同様の規準で評価しておシ、
摩耗深さは最大摩耗深さで示した。1) Laboratory test results Table 2 shows the results of an investigation using the test equipment shown in FIG. In Fig. 2, (11 is a test piece 69 corresponding to a cast alloy for tools), which is fixed by a holder (2) that is reciprocated by a hydraulic cylinder.
) is a test piece corresponding to the workpiece, which is fixed to a holder (4) rotated by a motor at an outer circumferential speed of 1 m /
At the same time as it rotates at S, it is heated and maintained at filoooC by high frequency induction. Table 2 shows the results of a friction test at a pressure of 200 kjLf for 5 minutes. In the table, the seizure resistance is determined by visual inspection of the surface condition of the test piece after the friction test. ○: No seizure When wear occurs uniformly without occurrence,
∆ Indicates a case where the friction surface is uniformly worn, but seizure occurs partially and the mating material adheres; ×: A case where seizure occurs and the mating material adheres to the entire friction surface. Further, the amount of wear was calculated from the width of the wear scar and expressed as the wear volume. If seizure occurs on the entire surface, accurate measurement is impossible due to adhesion of the other material, so it is excluded from the table. Several steel types were selected from among the test materials subjected to the physical test, and guide shoes for model drilling machines were made and a stretching test was conducted. Table 5 shows the results. The test results are diameter 40φ,
This is the result of stretching a hollow tube with a wall thickness of 7 m and a length of 200 m to a length of 400 m, and repeating this process 20 times. Third
The seizure resistance of the table was evaluated using the same criteria as in Table 2.
The wear depth is expressed as the maximum wear depth.
第５表
以上のように本発明の工具用開運合金鋼は従来の鋳造合
金工具鋼に比してすぐれた耐摩耗性、耐焼付き性を有し
ておシ、工具原単位の低減や製品品質、製管能率の向上
に大きく寄与することがわかる。As shown in Table 5 and above, the Kaiun alloy steel for tools of the present invention has superior wear resistance and seizure resistance compared to conventional cast alloy tool steel, reduces tool consumption, and improves product quality. It can be seen that this significantly contributes to improving pipe manufacturing efficiency.
添付図面において、第１図（ａ）、（ｋ＋）は本発明鋼
の鋳造組織（１）及び熱処理後の組織（ｂ）の顕微鏡写
真（ｘｓｏｏ）であシ、第２図は実験室的試験に使用し
た試験装置の説明図である。
士 ｌ 圀
”）（−１＞
ヤ ２ 図In the accompanying drawings, Figures 1 (a) and (k+) are micrographs (xsoo) of the cast structure (1) and the structure after heat treatment (b) of the steel of the present invention, and Figure 2 is a laboratory test. FIG. 2 is an explanatory diagram of the test equipment used in士 l 圀”)(-1＞ や 2 fig.
Claims (1)
Ｃｒ２０〜４０％、Ｎｉ２０〜５０％を含有し、残部Ｆ
ｅ及び不可避的不純物より成る鋳造高合金鋼を、固相線
より２０℃下の温度から固相線より４０℃高い温度まで
の温度範囲にて１〜２００時間加熱保持することを特徴
とする凝集、粗大化せしめた炭化物組織を有する耐摩耗
性、耐焼付き性良好な工具用鋳造合金の製造方法。 ２、Ｃ０．８〜２．５％、Ｓｉ３％以下、Ｍｎ３％以下
、Ｃｒ２０〜４０％、Ｎｉ２０〜５０％を含有し、さら
にＭｏ０．１〜５％、Ｗ０．１〜５％、Ｃｏ０．１ 〜
５％、Ｔｉ０．１〜５％、Ｖ０．１〜５％、Ｚｒ０．１
〜５％のうち１種又は２種以上を含み、残部Ｆｅ及び不
可避的不純物より成る鋳造高合金鋼を、固相線より２０
℃下の温度から固相線より４０℃高い温度までの温度範
囲にて１〜２０時間加熱、保持することを特徴とする凝
集、粗大化せしめた炭化物組織を有する耐摩耗性、耐焼
付き性良好な工具用鋳造合金の製造方法。[Claims] 1. 0.8 to 2.5%, Si 3% or less, Mn 3% or less,
Contains 20 to 40% Cr, 20 to 50% Ni, and the balance is F.
Agglomeration characterized by heating and holding a cast high alloy steel consisting of E and inevitable impurities at a temperature ranging from 20°C below the solidus line to 40°C above the solidus line for 1 to 200 hours. , a method for producing a casting alloy for tools having a coarse carbide structure and having good wear resistance and seizure resistance. 2. Contains 0.8-2.5% C, 3% Si or less, 3% Mn or less, 20-40% Cr, 20-50% Ni, and further Mo0.1-5%, W0.1-5%, Co0.1 ~
5%, Ti0.1-5%, V0.1-5%, Zr0.1
Cast high alloy steel containing one or more of ~5% and the balance Fe and unavoidable impurities is heated to 20% below the solidus line.
Good wear resistance and seizure resistance with agglomerated and coarsened carbide structure characterized by heating and holding for 1 to 20 hours in a temperature range from below ℃ to 40℃ higher than the solidus line. A method for manufacturing a casting alloy for tools.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP23513784A JPS61113713A (en) | 1984-11-09 | 1984-11-09 | Manufacture of cast alloy for tool |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP23513784A JPS61113713A (en) | 1984-11-09 | 1984-11-09 | Manufacture of cast alloy for tool |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS61113713A true JPS61113713A (en) | 1986-05-31 |
| JPH0419286B2 JPH0419286B2 (en) | 1992-03-30 |
Family
ID=16981602
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP23513784A Granted JPS61113713A (en) | 1984-11-09 | 1984-11-09 | Manufacture of cast alloy for tool |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS61113713A (en) |
-
1984
- 1984-11-09 JP JP23513784A patent/JPS61113713A/en active Granted
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0419286B2 (en) | 1992-03-30 |
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| Date | Code | Title | Description |
|---|---|---|---|
| EXPY | Cancellation because of completion of term |