JPH04263042A - Steel for molding die having high hardness and its manufacture - Google Patents
Steel for molding die having high hardness and its manufactureInfo
- Publication number
- JPH04263042A JPH04263042A JP4277091A JP4277091A JPH04263042A JP H04263042 A JPH04263042 A JP H04263042A JP 4277091 A JP4277091 A JP 4277091A JP 4277091 A JP4277091 A JP 4277091A JP H04263042 A JPH04263042 A JP H04263042A
- Authority
- JP
- Japan
- Prior art keywords
- steel
- hardness
- less
- temperature
- high hardness
- 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
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 44
- 239000010959 steel Substances 0.000 title claims abstract description 44
- 238000004519 manufacturing process Methods 0.000 title claims description 16
- 238000000465 moulding Methods 0.000 title description 5
- 230000032683 aging Effects 0.000 claims abstract description 21
- 238000001816 cooling Methods 0.000 claims abstract description 18
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 6
- 238000010438 heat treatment Methods 0.000 claims abstract description 5
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 5
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 4
- 239000012535 impurity Substances 0.000 claims abstract description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 4
- 238000012545 processing Methods 0.000 claims description 5
- 238000000034 method Methods 0.000 claims description 4
- 229910052802 copper Inorganic materials 0.000 abstract description 3
- 229910052759 nickel Inorganic materials 0.000 abstract description 3
- 229910052710 silicon Inorganic materials 0.000 abstract description 2
- 238000010137 moulding (plastic) Methods 0.000 abstract 1
- 239000000463 material Substances 0.000 description 18
- 230000000694 effects Effects 0.000 description 13
- 239000004033 plastic Substances 0.000 description 8
- 229920003023 plastic Polymers 0.000 description 8
- 230000000052 comparative effect Effects 0.000 description 7
- 238000004881 precipitation hardening Methods 0.000 description 7
- 239000000203 mixture Substances 0.000 description 6
- 238000010586 diagram Methods 0.000 description 5
- 238000005098 hot rolling Methods 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- 230000007423 decrease Effects 0.000 description 3
- 230000001376 precipitating effect Effects 0.000 description 3
- 239000000243 solution Substances 0.000 description 3
- 238000003483 aging Methods 0.000 description 2
- 229910001563 bainite Inorganic materials 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 229910000734 martensite Inorganic materials 0.000 description 2
- 238000011160 research Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 229910052717 sulfur Inorganic materials 0.000 description 2
- 229910000760 Hardened steel Inorganic materials 0.000 description 1
- 229910018651 Mn—Ni Inorganic materials 0.000 description 1
- 229910000943 NiAl Inorganic materials 0.000 description 1
- NPXOKRUENSOPAO-UHFFFAOYSA-N Raney nickel Chemical compound [Al].[Ni] NPXOKRUENSOPAO-UHFFFAOYSA-N 0.000 description 1
- 229910000746 Structural steel Inorganic materials 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 229910052797 bismuth Inorganic materials 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000005530 etching Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 239000003365 glass fiber Substances 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 239000011347 resin Substances 0.000 description 1
- 229920005989 resin Polymers 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 229910052711 selenium Inorganic materials 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
Landscapes
- Heat Treatment Of Steel (AREA)
Abstract
Description
【０００１】0001
【産業上の利用分野】本発明は成形金型、特にプラスチ
ック成形金型が主たる用途である析出硬化型構造用鋼お
よびその製造方法に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a precipitation-hardening structural steel whose main use is a mold, particularly a plastic mold, and a method for manufacturing the same.
【０００２】0002
【従来の技術】従来より、時効硬化性プラスチック金型
用鋼に関しては、例えば、電気製鋼Ｖｏｌ．４１，Ｎｏ
．１，２７〜３３頁（大同製鋼研究会発行）、特殊鋼第
２０巻，第４号，５８〜６１頁（特殊鋼倶楽部発行）、
特公昭５９−３７７４４号、特公昭６１−２２０２５号
、特開昭６０−６７６４１号などにおいて、Ｍｎ−Ｎｉ
−Ａｌ−Ｃｕ−Ｍｏ系の時効硬化性プラスチック金型用
鋼が開示されている。これらの鋼は、処理工程の概念図
である図１（ａ）に示されるような、溶体化熱処理の後
に５００℃前後での時効処理を施すことによって得られ
るもので、フォートエッチング加工性等に優れた特性を
有するものである。BACKGROUND OF THE INVENTION Conventionally, age-hardening steel for plastic molds has been described, for example, in Denki Steel Vol. 41,No.
．． 1, pp. 27-33 (published by Daido Steel Research Group), Special Steel Vol. 20, No. 4, pp. 58-61 (published by Special Steel Club),
Mn-Ni
An age-hardening steel for plastic molds based on -Al-Cu-Mo is disclosed. These steels are obtained by aging treatment at around 500°C after solution heat treatment, as shown in Figure 1(a), which is a conceptual diagram of the treatment process, and they have excellent properties such as fort etching processability. It has excellent properties.
【０００３】また、最近では特に厚肉の成形用金型材と
して、図１（ｂ）に示されるような、すなわち特定温度
で特定量の圧下を加える熱間圧延の後に４５０〜５５０
℃の温度範囲に１〜１００時間保持することによって得
られるＭｎ−Ｎｉ−Ａｌ−Ｃｕ−Ｍｏ系析出硬化鋼が特
開昭６３−１６２８１１号によって提案されている。[0003] Recently, as shown in Fig. 1(b), especially thick-walled mold materials have been developed, 450 to 550
JP-A-63-162811 proposes a Mn-Ni-Al-Cu-Mo precipitation hardened steel obtained by holding the steel in a temperature range of 1 to 100 hours.
【０００４】そして、このような従来の析出硬化鋼は、
前者が溶体化処理後に、後者が熱間圧延後にそれぞれ略
４５０〜５５０℃で時効処理がなされるものであるが（
図１（ａ）および（ｂ）参照）、いずれもその硬度はＨ
ＲＣ硬度値で４０前後となっている。[0004] Such conventional precipitation hardening steel is
The former is subjected to solution treatment and the latter is subjected to aging treatment at approximately 450 to 550°C after hot rolling.
(see Figures 1(a) and (b)), both have a hardness of H
The RC hardness value is around 40.
【０００５】[0005]
【発明が解決しようとする課題】しかし、最近のプラス
チック樹脂の種類あるいはプラスチック製品の多様化に
伴い、成形金型鋼材もより高硬度のものが要求されてき
ている。特に、最近ではガラス繊維などを含むプラスチ
ックを成形する金型としてＨＲＣ値で４５を上回る硬度
が要求される場合も出ており、従って従来の析出硬化鋼
ではプラスチック成形用金型として十分対応できない状
況にある。[Problems to be Solved by the Invention] However, with the recent diversification of types of plastic resins and plastic products, steel materials for molding molds are also required to have higher hardness. In particular, recently there are cases where molds for molding plastics containing glass fibers are required to have a hardness of over 45 in HRC value, and therefore conventional precipitation hardened steels are not able to adequately support molds for molding plastics. It is in.
【０００６】本発明は、以上のような問題に鑑み創案さ
れたもので、高い硬度を有し、特に近時のプラスチック
成形用金型として十分対応し得る鋼およびその製造方法
を提供しようとするものである。The present invention was devised in view of the above-mentioned problems, and it is an object of the present invention to provide a steel that has high hardness and can be used particularly as molds for molding plastics in recent years, and a method for manufacturing the same. It is something.
【０００７】[0007]
【課題を解決するための手段】本発明者らは、従来の析
出硬化鋼および図１（ａ）および（ｂ）に示される製造
法を参考にして各種実験・研究を行った結果、圧延ある
いは鍛造などの熱間加工条件とその後の冷却条件を制御
してＭｎ−Ｎｉ−Ａｌ−Ｃｕ−Ｍｏ鋼の組織と析出を制
御すること、および４５０℃以上５２５℃以下の温度で
時効処理することにより従来材に比べ高硬度の鋼を得る
ことに成功した。[Means for Solving the Problems] The present inventors have conducted various experiments and research with reference to conventional precipitation hardening steel and the manufacturing method shown in FIGS. 1(a) and (b), and have found that rolling or By controlling the hot working conditions such as forging and subsequent cooling conditions to control the structure and precipitation of Mn-Ni-Al-Cu-Mo steel, and by aging treatment at a temperature of 450°C or higher and 525°C or lower. We succeeded in obtaining a steel with higher hardness than conventional materials.
【０００８】すなわち本発明者らは、構成成分およびそ
の組成範囲が、重量％でＣ：０．０５〜０．２０％、Ｓ
ｉ：０．１０〜１．０％、Ｍｎ：０．８〜２．０％、Ｎ
ｉ：２．５〜３．５％、Ａｌ：０．５〜１．５％、Ｃｕ
：０．７〜１．７％、Ｍｏ：０．１〜０．５％ 、残部
Ｆｅおよび不可避不純物からなるものを、図１（ａ）に
示すような工程、具体的には加熱した後熱間加工するに
際し７００℃以上で加工を終了し、その後直ちに空冷以
上５０℃／ｓｅｃ以下の冷却速度で４００℃以下まで冷
却し、さらに４５０℃以上５２５℃以下の温度で１〜１
００時間時効処理することにより、ＨＲＣ値で４３を超
える硬度の鋼を得ることに成功したものである。That is, the present inventors have determined that the constituent components and their composition ranges are C: 0.05 to 0.20%, S: 0.05% to 0.20%, S:
i: 0.10-1.0%, Mn: 0.8-2.0%, N
i: 2.5-3.5%, Al: 0.5-1.5%, Cu
: 0.7 to 1.7%, Mo: 0.1 to 0.5%, the balance consisting of Fe and unavoidable impurities. When performing temporary processing, the processing is completed at 700°C or higher, and then immediately cooled to 400°C or lower at a cooling rate of not less than air cooling and not more than 50°C/sec, and then further cooled at a temperature of 450°C to 525°C for 1 to 1
By aging for 00 hours, we succeeded in obtaining steel with a hardness exceeding 43 in terms of HRC value.
【０００９】以下、この発明について詳細に説明する。The present invention will be explained in detail below.
【００１０】まず、本発明鋼の成分限定理由は次の通り
である。First, the reasons for limiting the composition of the steel of the present invention are as follows.
【００１１】Ｃ：Ｃは本発明鋼を熱間加工後に空冷また
は制御冷却した場合、マルテンサイトやベイナイト組織
の生成を容易ならしめる効果があるため重量％で（以下
同じ）０．０５〜０．２０％添加する。０．０５％を下
回ると組織制御の効果が認められなくなるのでこれを下
限とした。また、０．２０％を超える添加は、鋼の被削
性を害し、時効後の靱性を低下させるのでこれを上限と
した。C: C has the effect of facilitating the formation of martensite and bainite structures when the steel of the present invention is air-cooled or controlled cooled after hot working, so it is 0.05-0.05% by weight (the same applies hereinafter). Add 20%. If it is less than 0.05%, no effect on structure control will be observed, so this was set as the lower limit. Furthermore, addition of more than 0.20% impairs the machinability of the steel and reduces the toughness after aging, so this was set as the upper limit.
【００１２】Ｓｉ：Ｓｉは硬度を確保するために０．１
０〜１．０％の範囲で添加する。０．１０％を下回ると
硬度が確保できないのでこれを下限とした。また、１．
０％を上回ると延靱性と被削性を劣化させるのでこれを
上限とした。Si: Si is 0.1 to ensure hardness.
Add in a range of 0 to 1.0%. If it is less than 0.10%, hardness cannot be ensured, so this was set as the lower limit. Also, 1.
If it exceeds 0%, the ductility and machinability deteriorate, so this was set as the upper limit.
【００１３】Ｍｎ：ＭｎはＣやＳｉと同様に硬度を確保
するために０．８〜２．０％の範囲で添加する。０．８
％を下回ると硬度が確保できないのでこれを下限とした
。また、２．０％を上回ると延靱性と被削性を劣化させ
るのでこれを上限とした。Mn: Like C and Si, Mn is added in a range of 0.8 to 2.0% to ensure hardness. 0.8
%, hardness cannot be ensured, so this was set as the lower limit. Further, if it exceeds 2.0%, the ductility and machinability deteriorate, so this was set as the upper limit.
【００１４】Ｎｉ：本発明鋼においてＮｉはその一部が
Ｃｕと全率固溶して熱間加工における赤熱脆性を防ぎ、
熱間圧延後の冷却状態で焼入れ性を増加し硬度を確保す
る。また時効状態ではＡｌとともにＮｉＡｌ相を形成し
高硬度を確保する必須成分であるため２．５〜３．５％
添加する。２．５％を下回ると硬度が確保できないので
これを下限とした。また、３．５％を上回ると延靱性と
被削性に悪影響があるのでこれを上限とした。Ni: In the steel of the present invention, a part of Ni is completely dissolved in solid solution with Cu to prevent red brittleness during hot working,
Hardenability is increased and hardness is ensured in the cooled state after hot rolling. In addition, in the aged state, it forms a NiAl phase with Al and is an essential component that ensures high hardness, so 2.5 to 3.5%
Added. If it is less than 2.5%, hardness cannot be ensured, so this was set as the lower limit. Further, if it exceeds 3.5%, it will have a negative effect on ductility and machinability, so this was set as the upper limit.
【００１５】Ａｌ：ＡｌはＮｉとともに時効状態でＮｉ
Ａｌ相を析出させるための必須成分であり、０．５〜１
．５％添加する。
０．５％を下回ると硬度への効果が小さくなるのでこれ
を下限とした。また、１．５％を上回ると製造性、鏡面
仕上げ性および延靱性を害するためこれを上限とした。Al: Al and Ni in the aged state
It is an essential component for precipitating the Al phase, and has a content of 0.5 to 1
．． Add 5%. If it is less than 0.5%, the effect on hardness will be reduced, so this was set as the lower limit. Moreover, if it exceeds 1.5%, the manufacturability, mirror finish, and ductility are impaired, so this was set as the upper limit.
【００１６】Ｃｕ：Ｃｕは時効状態においてε−Ｃｕ相
を析出させるための核として重要な役割を持つほか、被
削性の改善に効果があるので０．７〜１．７％添加する
。０．７％を下回るとこれらの効果が小さくなるのでこ
れを下限とした。また、１．７％を上回ると製造時の表
面疵や経済性などの点で不利になるのでこれを上限とし
た。Cu: Cu plays an important role as a nucleus for precipitating the ε-Cu phase in the aged state, and is also effective in improving machinability, so it is added in an amount of 0.7 to 1.7%. If the content is less than 0.7%, these effects will be reduced, so this was set as the lower limit. Moreover, if it exceeds 1.7%, it becomes disadvantageous in terms of surface flaws during manufacturing and economical efficiency, so this is set as the upper limit.
【００１７】Ｍｏ：Ｍｏは組織の均一化および強度・靱
性の改善を目的として０．１〜０．５％添加する。０．
１％を下回るとこれらの効果が認められなくなるのでこ
れを下限とした。また、０．５％を上回ると硬度が高く
なりすぎ被削性や延靱性に悪影響があるのでこれを上限
とした。Mo: Mo is added in an amount of 0.1 to 0.5% for the purpose of making the structure uniform and improving strength and toughness. 0.
If it is less than 1%, these effects will not be observed, so this was set as the lower limit. Moreover, if it exceeds 0.5%, the hardness becomes too high, which has an adverse effect on machinability and ductility, so this is set as the upper limit.
【００１８】本発明鋼はＨＲＣ４３を超える硬度で金型
に加工されるため被削性を確保することが必要である。
そのためにＳを０．３％まで添加しても良い。Since the steel of the present invention has a hardness exceeding HRC43 and is processed into a mold, it is necessary to ensure machinability. For this purpose, S may be added up to 0.3%.
【００１９】なお、大型の金型に本発明鋼を適用する場
合、焼入性を確保するために、Ｃｒ：０．２１〜２．５
０％、Ｗ：０．５％以下、Ｃｏ：０．５％以下、Ｂｅ：
０．５％以下、Ｂ：０．０１％以下の少なくとも一種ま
たは二種以上選択して添加しても良い。また、結晶粒度
を微細化して靱性を向上させるためにＴｉ：０．５％以
下、Ｎｂ＋Ｔａ：０．３％以下、Ｚｒ：０．５％以下の
少なくとも一種または二種以上選択して添加しても良い
。さらに、被削性を向上させるために、Ｐｂ：０．０３
〜０．４％、Ｓｅ：０．０３〜０．５％、Ｔｅ：０．０
１〜０．３％、Ｂｉ：０．０２〜０．３％の少なくとも
一種または二種以上選択して添加しても良い。[0019] When applying the steel of the present invention to a large mold, Cr: 0.21 to 2.5 is required to ensure hardenability.
0%, W: 0.5% or less, Co: 0.5% or less, Be:
At least one or two or more types of B: 0.5% or less and B: 0.01% or less may be selected and added. In addition, in order to refine the grain size and improve toughness, at least one or two or more of Ti: 0.5% or less, Nb+Ta: 0.3% or less, and Zr: 0.5% or less are added. Also good. Furthermore, in order to improve machinability, Pb: 0.03
~0.4%, Se: 0.03~0.5%, Te: 0.0
At least one or two or more of Bi: 1 to 0.3% and Bi: 0.02 to 0.3% may be selected and added.
【００２０】次に、製造条件について説明する。Next, manufacturing conditions will be explained.
【００２１】前述した組成の鋼を加熱するに当たっては
加熱温度を１３００〜９５０℃の範囲とするのが好まし
い。９５０℃未満では各種成分の固溶が十分でなく時効
後の硬度が低下する可能性がある。また、１３００℃を
超えるとスケール生成または粒界溶融による熱間加工性
の低下の恐れがあるためである。[0021] When heating the steel having the above-mentioned composition, the heating temperature is preferably in the range of 1300 to 950°C. If the temperature is lower than 950°C, solid solution of various components may not be sufficient and the hardness after aging may decrease. Furthermore, if the temperature exceeds 1300°C, there is a risk of deterioration in hot workability due to scale formation or grain boundary melting.
【００２２】熱間圧延するに際し７００℃以上で加工を
終了するのは、加工仕上り温度がこの温度を下回ると、
変態点近傍の冷却の効果が少なくなり組織制御の効果が
認められなくなるためと材質の異方性が増すためこれを
下限とした。[0022] The reason for finishing hot rolling at 700°C or higher is that if the finishing temperature falls below this temperature,
This was set as the lower limit because the effect of cooling near the transformation point decreases and the effect of microstructure control is no longer recognized, and the anisotropy of the material increases.
【００２３】加工率については時効時の析出サイトの分
散効果を確保するため少なくとも５％の加工率が必要で
ある。Regarding the working rate, a working rate of at least 5% is required to ensure the effect of dispersing the precipitation sites during aging.
【００２４】熱間加工後に直ちに空冷以上５０℃／ｓｅ
ｃ以下の冷却速度で冷却するのは、鋼の組織をマルテン
サイトあるいはベイナイトなどの組織にするためと、加
工後の冷却中にＮｉ、Ａｌ、Ｃｕなどの析出硬化型元素
が一部析出することを抑制し、その後の時効時の析出硬
化に、より有効に寄与させるためである。空冷より小さ
な冷却速度では、上記の効果が認められないためこれを
下限とした。５０℃／ｓｅｃを超える冷却速度では焼割
れなどの製造上の問題が生ずるためこれを上限とした。Immediately after hot working, air cooling at 50°C/se or higher
The reason for cooling at a cooling rate of less than c is to change the structure of the steel to martensite or bainite, and to prevent some precipitation hardening elements such as Ni, Al, and Cu from precipitating during cooling after processing. The purpose is to suppress this and contribute more effectively to precipitation hardening during subsequent aging. Since the above effect was not observed at a cooling rate lower than that of air cooling, this was set as the lower limit. A cooling rate exceeding 50° C./sec causes manufacturing problems such as quench cracking, so this was set as the upper limit.
【００２５】時効温度は、本発明の高温時効の観点から
４５０〜５２５℃に限定した。これは時効温度と硬度と
の相関関係を示す図２より明らかなように、４５０℃を
下回ると十分な硬度が得られないためこれを下限とする
一方で、５２５℃を上回ると過時効となり硬度が低くな
るのでこれを上限とした。The aging temperature was limited to 450 to 525°C from the viewpoint of high temperature aging of the present invention. As is clear from Figure 2, which shows the correlation between aging temperature and hardness, if the temperature falls below 450°C, sufficient hardness cannot be obtained, so this is set as the lower limit, while if it exceeds 525°C, overaging occurs and the hardness decreases. This was set as the upper limit because it would be low.
【００２６】時間については、１時間であれば十分であ
る一方で、１００時間を超えると過時効になるので、１
〜１００時間の範囲とした。Regarding the time, while 1 hour is sufficient, if it exceeds 100 hours, it will be overdue, so 1 hour is sufficient.
It was set as the range of ~100 hours.
【００２７】[0027]
【実施例】以下、この発明の実施例について具体的に説
明する。[Examples] Examples of the present invention will be described in detail below.
【００２８】下表に試験に用いた鋼材の組成、製造条件
と硬度を示す。そのうち、表１には鋼材の成分組成を、
表２には本発明材と比較材の製造条件と硬度をそれぞれ
示す。The table below shows the composition, manufacturing conditions, and hardness of the steel materials used in the test. Among them, Table 1 shows the composition of steel materials,
Table 2 shows the manufacturing conditions and hardness of the present invention material and comparative material, respectively.
【００２９】[0029]
【表１】[Table 1]
【００３０】[0030]
【表２】[Table 2]
【００３１】表１中鋼Ａ〜Ｄはいずれも本発明の組成範
囲に合致するものであり、また表２中番号１〜１２は本
発明の製造条件をすべて満足させる実施例である。同表
からも明らかなように、本発明材は全てＨＲＣ値が４３
以上となっており、特に番号４、１１、１２の鋼材はＨ
ＲＣ値が４５と高硬度となっている。Steels A to D in Table 1 all meet the composition range of the present invention, and numbers 1 to 12 in Table 2 are examples that satisfy all of the manufacturing conditions of the present invention. As is clear from the same table, all the materials of the present invention have an HRC value of 43.
Above are the steel materials numbered 4, 11, and 12 in particular.
It has a high hardness with an RC value of 45.
【００３２】表２中番号１３〜１９は、いずれかの製造
条件が本発明の範囲外となる比較例である。このうち、
番号１３は時効温度が本発明の範囲より低く設定された
比較鋼材である。同表、および時効温度と硬度との相関
関係を示す上述の図２より明らかなように、この比較鋼
材は本発明材よりＨＲＣ値が下回っている。次に、番号
１４は時効時間が長く設定される比較鋼材であるが、や
はり過時効のため硬度が低い結果となっている。番号１
５は時効処理をしない比較鋼材であるがやはり硬度が不
充分である。次に、番号１６〜１８は、図１（ａ）に示
すような従来の製造方法によって得られた鋼材、すなわ
ち固溶化熱処理を施しその後時効した比較鋼材であるが
硬度がＨＲＣ値で３８〜４０と低い値である。また番号
１９は図１（ｂ）に示すような熱間圧延後に等温保持し
た比較鋼材である。この場合もやはり、時効温度が５２
０℃では低い硬度しか得られないことが分かる。[0032] Numbers 13 to 19 in Table 2 are comparative examples in which any of the manufacturing conditions were outside the scope of the present invention. this house,
Number 13 is a comparative steel material whose aging temperature is set lower than the range of the present invention. As is clear from the same table and the above-mentioned FIG. 2 showing the correlation between aging temperature and hardness, this comparative steel material has a lower HRC value than the present invention material. Next, No. 14 is a comparison steel material for which the aging time is set for a long time, but the hardness is still low due to overaging. number 1
Comparative steel material No. 5 is not subjected to aging treatment, but its hardness is still insufficient. Next, numbers 16 to 18 are comparative steel materials obtained by the conventional manufacturing method as shown in FIG. This is a low value. Moreover, number 19 is a comparative steel material that is maintained at an isothermal temperature after hot rolling as shown in FIG. 1(b). Again, the aging temperature is 52
It can be seen that only low hardness can be obtained at 0°C.
【００３３】[0033]
【発明の効果】以上説明したように本発明によれば、固
溶化処理温度を省略した上、析出硬化型鋼を時効するこ
とによってＨＲＣ値で４３ポイント以上の高い硬度の鋼
材を得ることができ、金型使用時の鏡面性、精度、寿命
の点で大きな効果が期待できる。[Effects of the Invention] As explained above, according to the present invention, by omitting the solution treatment temperature and aging precipitation hardening steel, it is possible to obtain a steel material with high hardness with an HRC value of 43 points or more. Great effects can be expected in terms of specularity, precision, and lifespan when using molds.
【図１】鋼の製造条件を示す概念図であり、（ａ）およ
び（ｂ）は従来の析出硬化型鋼、（ｃ）は本発明鋼の製
造条件を示す図である。FIG. 1 is a conceptual diagram showing the manufacturing conditions of steel; (a) and (b) are diagrams showing the manufacturing conditions of conventional precipitation hardening steel, and (c) is a diagram showing the manufacturing conditions of the steel of the present invention.
【図２】時効温度とＨＲＣ値との相関関係を示す図であ
る。FIG. 2 is a diagram showing the correlation between aging temperature and HRC value.
Claims (2)
Ｓｉ：０．１０〜１．０％、Ｍｎ：０．８〜２．０％、
Ｎｉ：２．５〜３．５％、Ａｌ：０．５〜１．５％、Ｃ
ｕ：０．７〜１．７％、Ｍｏ：０．１〜０．５％ 、残
部Ｆｅおよび不可避不純物からなり、加熱した後熱間加
工するに際し７００℃以上で加工を終了し、その後直ち
に空冷以上５０℃／ｓｅｃ以下の冷却速度で４００℃以
下まで冷却し、さらに４５０℃以上５２５℃以下の温度
で１〜１００時間時効処理することによって得られるこ
とを特徴とする高硬度の成形金型用鋼。Claim 1: C: 0.05 to 0.20% by weight;
Si: 0.10-1.0%, Mn: 0.8-2.0%,
Ni: 2.5-3.5%, Al: 0.5-1.5%, C
U: 0.7-1.7%, Mo: 0.1-0.5%, the balance consists of Fe and unavoidable impurities, and when hot working after heating, the processing is completed at 700°C or higher, and then immediately air cooled. For a mold with high hardness, characterized in that it is obtained by cooling to 400°C or less at a cooling rate of 50°C or more and 50°C or less, and then aging for 1 to 100 hours at a temperature of 450°C or more and 525°C or less. steel.
Ｓｉ：０．１０〜１．０％、Ｍｎ：０．８〜２．０％、
Ｎｉ：２．５〜３．５％、Ａｌ：０．５〜１．５％、Ｃ
ｕ：０．７〜１．７％、Ｍｏ：０．１〜０．５％ 、残
部Ｆｅおよび不可避不純物からなる鋼を、加熱した後熱
間加工するに際し７００℃以上で加工を終了し、その後
直ちに空冷以上５０℃／ｓｅｃ以下の冷却速度で４００
℃以下まで冷却し、さらに４５０℃以上５２５℃以下の
温度で１〜１００時間時効処理することを特徴とする高
硬度の成形金型用鋼の製造方法。[Claim 2] C: 0.05 to 0.20% by weight;
Si: 0.10-1.0%, Mn: 0.8-2.0%,
Ni: 2.5-3.5%, Al: 0.5-1.5%, C
When hot working steel consisting of u: 0.7 to 1.7%, Mo: 0.1 to 0.5%, balance Fe and unavoidable impurities, the processing is completed at 700°C or higher, and then Immediately air cooled to 400℃ at a cooling rate of 50℃/sec or less.
A method for manufacturing a high-hardness steel for forming molds, which comprises cooling to a temperature of 450° C. or lower and further aging treatment at a temperature of 450° C. or higher and 525° C. or lower for 1 to 100 hours.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP4277091A JPH04263042A (en) | 1991-02-15 | 1991-02-15 | Steel for molding die having high hardness and its manufacture |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP4277091A JPH04263042A (en) | 1991-02-15 | 1991-02-15 | Steel for molding die having high hardness and its manufacture |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH04263042A true JPH04263042A (en) | 1992-09-18 |
Family
ID=12645208
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP4277091A Pending JPH04263042A (en) | 1991-02-15 | 1991-02-15 | Steel for molding die having high hardness and its manufacture |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH04263042A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2011153346A (en) * | 2010-01-27 | 2011-08-11 | Daido Steel Co Ltd | Method for manufacturing resin molding die |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS58221262A (en) * | 1982-11-01 | 1983-12-22 | Daido Steel Co Ltd | Age hardening steel for metallic mold for plastic |
| JPS6067641A (en) * | 1983-09-22 | 1985-04-18 | Daido Steel Co Ltd | Steel for aging hardened plastic mold |
| JPS6267152A (en) * | 1985-09-18 | 1987-03-26 | Hitachi Metals Ltd | Tool steel for hot working |
| JPS63162811A (en) * | 1986-12-26 | 1988-07-06 | Kawasaki Steel Corp | Manufacture of precipitation-hardening steel |
-
1991
- 1991-02-15 JP JP4277091A patent/JPH04263042A/en active Pending
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS58221262A (en) * | 1982-11-01 | 1983-12-22 | Daido Steel Co Ltd | Age hardening steel for metallic mold for plastic |
| JPS6067641A (en) * | 1983-09-22 | 1985-04-18 | Daido Steel Co Ltd | Steel for aging hardened plastic mold |
| JPS6267152A (en) * | 1985-09-18 | 1987-03-26 | Hitachi Metals Ltd | Tool steel for hot working |
| JPS63162811A (en) * | 1986-12-26 | 1988-07-06 | Kawasaki Steel Corp | Manufacture of precipitation-hardening steel |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2011153346A (en) * | 2010-01-27 | 2011-08-11 | Daido Steel Co Ltd | Method for manufacturing resin molding die |
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