CN102102164A - Metal mould steel with excellent thermal machinability - Google Patents
Metal mould steel with excellent thermal machinability Download PDFInfo
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- CN102102164A CN102102164A CN 201010615010 CN201010615010A CN102102164A CN 102102164 A CN102102164 A CN 102102164A CN 201010615010 CN201010615010 CN 201010615010 CN 201010615010 A CN201010615010 A CN 201010615010A CN 102102164 A CN102102164 A CN 102102164A
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Abstract
The present invention provides metal mould steel which has excellent machinability, high rusting resistance and high thermal machinability and has strength and toughness that satisfy the requirement of being used as a metal mould product. The metal mould steel comprises the following components by mass: 0.1-less than 0.2% of C; larger than 0-1.2% of Si; 1.2-2.0% of Mn; 0.01-0.1% of S; 0.5-1.5% of Ni, 12.0-13.0% of Cr; 0.3-0.8% of Mo; 0.07-0.3% of V; 0.1-1.0% of Cu; less than 0.05% of Al; 0.03-0.1% of N; and the balance of Fe and inevitable impurity. Preferably, the percentage of Si is 0.1-0.8%; the percentage of S is 0.05-0.1%; the percentage of N is 0.04-0.1%; and the percentage of the inevitable impurity O is less than 0.02%. Alternatively, the hardness of the metal mould steel is 30-45 HRC.
Description
Technical field
The present invention relates to metal die for moulding, relate to the metal pattern steel on the mold part of the die insert that is used to constitute its die cavity portion etc., the die holder that keeps die insert etc. as plastics, rubber.
Background technology
In the past, in the metal pattern of moulding plastics etc., the metal pattern that constitutes it was required the excellent performance that is cut with steel.And in the integral body of these metal patterns, processing is used to fit big " the die insert hole " of maintenance as the die insert of metal pattern body on the die holder that forms its shell.Therefore, with in the steel, particularly die holder requires the more excellent performance that is cut with steel at metal pattern.In addition, this die holder is provided with the water-cooled hole that is used to shorten shaping cycle, so, also require excellent anti-getting rusty property to water etc.
Using always with steel as above-mentioned die holder that C-Mn-Cr-Mo-Fe is a steel in JIS-SCM440 etc. low-alloyed.And in recent years, in order to adapt to the strong request of the shortening of making delivery date, the reduction of process cost etc., general use is added fast machinability and is given element S and improved the metal pattern steel (patent documentation 1) that is cut performance.In addition, also having proposed on the basis of adding S, is purpose to improve anti-getting rusty property, further makes the tool steel (patent documentation 2,3) of low-carbon (LC).
The prior art document
Patent documentation
Patent documentation 1: Japanese kokai publication hei 03-097829 communique
Patent documentation 2: Japanese kokai publication hei 05-279800 communique
Patent documentation 3: Japanese Unexamined Patent Application Publication 2008-505786 communique
Summary of the invention
The metal pattern of patent documentation 1 is cut the performance excellence with steel.But, having in quality % (below, be labeled as %), C:0.20% one-tenth above and the high Cr of middle C-that Cr:14% is above is grouped into, so if separate out thick carbide, then there is the worry that is difficult to stably manufacture a product in the hot workability variation.
Relative therewith, the metal pattern steel of patent documentation 2 with the level that C reduces to 0.1%, suppressed because carbide causes that being cut performance reduces, and hot workability is also good.But, because the reduction of the hardness that low Cization causes is to replenish by separating out of NiAl intermetallic compound, so need to add the Al more than 0.5%.Therefore, be non-metallic inclusion if form the aluminium of hard, then exist to reduce to be cut performance or hot worry.Particularly, for steel, the aluminium in the matrix is that non-metallic inclusion will become the principal element that forms pin hole, makes the polishability variation, so be the factor that get rid of for the plastic shaping metal pattern.
The metal pattern steel of patent documentation 3, because C is extremely reduced to below 0.09%, though hot workability, anti-getting rusty property excellence,, when reaching the above high rigidity of 30HRC, be difficult to it is stably obtained.
Therefore, the invention provides a kind of metal pattern steel, each characteristic that it can't all satisfy with steel at the metal pattern of keeping in the past, promptly as intensity, the toughness of metal pattern with steel, particularly the die holder of plastic shaping metal pattern is with on the desired basis that is cut performance and anti-getting rusty property of steel, also has both excellent its steel manufacturing to be become be easy to hot workability.
The present inventor has restudied and has made metal pattern not damage in the past the method that performance and anti-getting rusty property just can reach excellent hot workability that is cut with steel.Its result, the principal element that has obtained the reduction hot workability is thick carbide or MnS inclusion, with the effective opinion of these miniaturization meetings.And, when finding to make the carbide miniaturization, there is the relation that constitutes the C content and the Cr content of this only narrow range, in addition,,, do not allow the addition of degree in the past in order to make the miniaturization of this MnS inclusion even add S.And, according to these opinions, follow the reduction of hardness of the reduction of C and Cr content to replenish, have both enough metal pattern steel that is cut performance and anti-getting rusty property, excellent hot workability thereby reached by Si, the Mo that adjusts other, the content of V, Cu.
That is to say, the present invention is a kind of metal pattern steel that has superior hot workability, it is characterized in that, comprise: in quality %, C:0.1～less than 0.2%, Si: greater than 0～1.2%, Mn:1.2～2.0%, S:0.01～0.1%, Ni:0.5～1.5%, Cr:12.0～13.0%, Mo:0.3～0.8%, V:0.07～0.3%, Cu:0.1～1.0%, below the Al:0.05%, N:0.03～0.1%, surplus is Fe and unavoidable impurities.Preferably, Si is 0.1～0.8%, S is 0.05～0.1%, N is 0.04～0.1%, and unavoidable impurities O is below 0.02%.Perhaps, further, metal pattern is 30～45HRC with the hardness of steel.
Because the present invention has had both intensity, toughness, has been cut performance, anti-getting rusty property, make each characteristic that relevant hot workability metal pattern so in the past can't all satisfy with steel with its steel in addition, thus the processing number of times when helping the metal pattern making significantly reduce and improve characteristic as metal pattern.Therefore, be raising otherwise effective technique for the technology of metal pattern.
Description of drawings
Fig. 1 is illustrated in anti-the getting rusty property test of embodiment 1 figure of the situation of getting rusty that produces on the polished surface of steel 1～4 of the present invention and comparative steel 1～6.
Fig. 2 is for illustrating in embodiment 2 figure of the tempered-hardness of steel 3 of the present invention and comparative steel 3.
Embodiment
Metal pattern of the present invention with steel with the alloy of low C-Mn-Ni-Cr-Fe system as basal component.Wherein, be 0.1 to less than 0.2% by making C, reached the high rigidity of 30～45HRC with for example high tempering more than 550 ℃.In addition, be 12.0～13.0% high-content by making Cr, a large amount of Cr is solid-solubilized in the matrix, form fine and close oxide film, give excellent anti-getting rusty property.When using as metal pattern, excellent anti-getting rusty property will prevent getting rusty of above-mentioned water-cooled hole, and cooling performance is continued for a long time, help the raising in metal pattern life-span.
And, being cut the metal pattern steel of the present invention of performance excellence, can supply with the pre-hard state of 30 for example above-mentioned～45HRC.That is,, after mechanical workout such as cutting under this hardness state, implement polished finish and be organized into this shape and be used for the component shape of regulation.Therefore, owing to can omit thermal treatment after the above-mentioned processing, so also can be used for the mold part of strict dimensional precision.
Below, the reason that the composition of steel of the present invention limits is narrated.
C is used to keep metal pattern intensity, preferably keeps the necessary basic interpolation element of Q-tempering hardness about 30～45HRC.And the machining deformation that takes place when suppressing machining etc. preferably reduces the residual stress in the steel, for this reason, needs to raise above-mentioned tempering temperature.Therefore, in steel of the present invention, importantly only add make as the tempering more than 550 ℃ in can stably reach hardness more than the 30HRC enough C amount.But,, make to be cut performance, hot workability reduction if too much, then form huge residual carbide.Therefore, C is 0.1 to less than 0.2%.
Si is the element that adds as reductor when steel ingot is made.And, be to have by being contained to improve the element that is cut the impact of performance in steel of the present invention.If too much, then can cause the reduction of mechanical propertys such as toughness, institute thinks below 1.2%.Be preferably more than 0.1% and/or below 0.8%.
Mn is in order to improve the hardenability of steel of the present invention, suppresses ferritic generation and gives suitable Q-tempering hardness and the important element that adds.But,, then make the viscosity increase reduction of matrix be cut performance if too much.Therefore, Mn is 1.2～2.0%.Be preferably below 1.7%.
S is by being present in non-metallic inclusion MnS form in the tissue and the raising that is cut performance is had very big effect.But the existence of a large amount of MnS will become the growth encourage mechanical characteristics, and flexible anisotropy etc. particularly reduces the principal element of the performance of metal pattern self.In addition, in the manufacturing processed of steel, thick MnS will hinder hot workability.Therefore, in the present invention, S is 0.01～0.1%.To be cut performance in order improving, preferably to contain more than 0.05%.
Ni is the viscosity that is used to increase matrix, improves the important element of flexible.But,, make toughness and the balance variation that is cut performance if too much, it is sticking then can to become.Therefore, be 0.5～1.5%.Be preferably more than 0.8% and/or below 1.3%.
Cr is solid-solubilized in the matrix, improves the extremely important element of anti-the getting rusty property of steel of the present invention.In addition, in temper, for the carbide that generates Cr system forms the intensity of steel of the present invention and adds.If too much, then can cause hot workability and the deterioration that is cut performance.Therefore, Cr is 12.0～13.0%.
Mo separates out when tempering and the aggegation fine carbide, thereby improves the intensity and the temper softening resistance of steel of the present invention.Further, the part of Mo is by in the oxide film thereon that is solid-solubilized in the metal pattern surface, thus have improve metal pattern in using, for example to the action effect of the erosion resistance of the corrosive gases that from plastics, produces.But, on the other hand,, then become the principal element that is cut the performance reduction if too much.Therefore, Mo is 0.3～0.8%.Be preferably more than 0.4% and/or below 0.6%.
When V improves the temper softening resistance, suppress thickization of crystal grain, help to improve toughness.In addition, has the carbide that forms hard imperceptibly and the effect that improves wear resistance.Need V at least more than 0.07% for this reason, still, if too much, then cause the reduction that is cut performance, so V is below 0.3%.Be preferably below 0.25%.
Cu is solid-solubilized in the matrix by a part and multiplies each other with the effect of above-mentioned Cr, further improves anti-the getting rusty property of steel of the present invention.A part is separated out from matrix in addition, thereby appropriateness reduces the ductility of matrix, gives the excellent performance that is cut.But,, except reducing hot workability, also reduce being cut performance on the contrary if too much.Therefore, Cu is 0.1～1.0%.Be preferably more than 0.2% and/or below 0.6%.
The deoxidant element of Al during usually as melting is used, its result, and the aluminium of generation is non-metallic inclusion (Al
2O
3If) remain in a large number in the steel, polishing processibility or hot workability are reduced.Therefore, the present invention need be defined as Al below 0.05%.Be preferably below 0.04%.
N (nitrogen) has the effect that improves anti-getting rusty property by its interpolation.In addition, be the element that in steel, forms fine nitride, have the effect of the hardness that improves steel of the present invention.Further, in machinability, in steel, form under the situation of fine nitride,, improve the effect that is cut performance so also be because these can improve the notch effect (notch effect) that cuts when forming.But, if add excessive nitrogen, then forming too much thick nitride, this becomes the toughness that makes metal pattern, the principal element that is cut performance and the remarkable deterioration of abrasive property.Therefore, the N of steel of the present invention is 0.03～0.1%.Be preferably more than 0.04%.
O (oxygen) as unavoidable impurities is the element that forms oxide compound in steel, and this is the principal element that makes cold plasticity processibility and the remarkable deterioration of abrasive property.And, particularly in the present invention, importantly suppress above-mentioned Al
2O
3Formation, so preferably O is controlled to be lower.Therefore, preferred order is followed successively by, and is limited to 0.02% on preferred, further is below 0.01%, more preferably below 0.005%.In addition, for the present invention of the reduction management of also carrying out Al simultaneously,, be about 0.001% also can bring into play effect of the present invention with the O amount if consider the easiness of its manufacturing.
Embodiment 1
The chemical constitution of having represented steel of the present invention and comparative steel in the table 1.In addition, comparative steel 1,2 is equivalent to the metal pattern steel of above-mentioned patent documentation 1, and comparative steel 3 is equivalent to the metal pattern steel of patent documentation 2, and comparative steel 4 is equivalent to the metal pattern steel of patent documentation 3.
Table 1
(quality %)
| Sample | C | Si | Mn | P | S | Ni | Cr |
| Steel 1 of the present invention | 0.14 | 1.03 | 1.45 | 0.006 | 0.060 | 1.05 | 12.16 |
| Steel 2 of the present invention | 0.13 | 1.02 | 1.45 | 0.007 | 0.050 | 1.02 | 12.32 |
| Steel 3 of the present invention | 0.16 | 0.60 | 1.46 | 0.005 | 0.064 | 1.06 | 12.71 |
| Steel 4 of the present invention | 0.14 | 0.60 | 1.41 | 0.005 | 0.065 | 1.06 | 12.72 |
| Comparative steel 1 | 0.35 | 0.35 | 1.65 | 0.007 | 0.070 | 0.01 | 15.89 |
| Comparative steel 2 | 0.33 | 0.23 | 1.74 | 0.006 | 0.093 | 0.44 | 15.93 |
| Comparative steel 3 | 0.05 | 0.20 | 1.43 | 0.006 | 0.152 | 0.27 | 12.38 |
| Comparative steel 4 | 0.17 | 0.37 | 1.33 | 0.005 | 0.002 | 3.06 | 13.22 |
| Comparative steel 5 | 0.14 | 0.59 | 1.55 | 0.006 | 0.058 | 1.10 | 12.68 |
| Comparative steel 6 | 0.16 | 0.59 | 1.43 | 0.005 | 0.055 | 1.05 | 12.82 |
| Sample | W | Mo | V | Cu | Al | |
0 | Fe ※ |
| Steel 1 of the present invention | ＜0.01 | 0.51 | 0.10 | 0.41 | 0.05 | 0.040 | 0.002 | Surplus |
| Steel 2 of the present invention | ＜0.01 | 0.51 | 0.10 | 0.21 | 0.05 | 0.040 | 0.002 | Surplus |
| Steel 3 of the present invention | ＜0.01 | 0.50 | 0.15 | 0.40 | 0.03 | 0.076 | 0.003 | Surplus |
| Steel 4 of the present invention | ＜0.01 | 0.50 | 0.15 | 0.40 | 0.03 | 0.031 | 0.004 | Surplus |
| Comparative steel 1 | ＜0.01 | 0.01 | 0.01 | 0.01 | 0.04 | 0.040 | 0.003 | Surplus |
| Comparative steel 2 | ＜0.01 | 0.01 | 0.01 | 0.01 | 0.02 | 0.001 | 0.006 | Surplus |
| Comparative steel 3 | ＜0.01 | 0.50 | 0.04 | 0.34 | 0.02 | 0.067 | 0.005 | Surplus |
| Comparative steel 4 | ＜0.01 | 0.34 | 0.01 | 0.01 | 1.06 | 0.001 | 0.001 | Surplus |
| Comparative steel 5 | ＜0.01 | 0.49 | 0.15 | 0.40 | 0.09 | 0.117 | 0.002 | Surplus |
| Comparative steel 6 | ＜0.01 | 0.48 | 0.14 | 0.39 | 0.03 | 0.002 | 0.003 | Surplus |
※ is impure
After these samples are carried out quench treatment from 1030 ℃, be that target is carried out temper with the hardness of 40HRC, modified hardness to regulation.Then, to modified steel of the present invention and comparative steel, implement its mechanical characteristics evaluation, following be cut test and the anti-test of getting rusty.Mechanical characteristics has been measured according to the impact value of 2mmU test with notched test piece, the tensile strength according to 1100 ℃ tension tests, elongation, relative reduction in area.Tension test is used to estimate the hot workability relevant with this steel manufacturing.
Being cut test is that above-mentioned sample after modified is implemented
Boring processing, use comparative steel 1 as 100 the hole count (this index more big, be cut performance more excellent) of its boring of index assessment during the life-span.The anti-test of getting rusty is on the face with the 20mm * 40mm after the polishing of above-mentioned sample, with 35 ℃ 5%NaCl aqueous solution sprayings 3 hours, uses comparative steel 1 as its rust area of index assessment (this index is more little, and anti-getting rusty property is excellent more) of 100.The steel of the present invention of this moment and the situation of getting rusty of comparative steel are as shown in Figure 1.And, above table of induction as a result is shown in table 2.
Table 2
According to table 2 as can be known, steel 1～4 of the present invention is kept the performance that is cut with comparative steel 1 equal excellence, and its hot workability is improved simultaneously, and toughness surpasses in the steel of the present invention 3,4 of 40HRC hardness also very excellent at modified one-tenth.And particularly the anti-personality of getting rusty of the steel of the present invention 1～3 that the N amount is high is outer excellent.
Relative therewith, than steel of the present invention, comparative steel 2 is high C, high Cr, so it is many that residual carbide becomes, hot workability reduces.And further, the N amount is also few, and the breach effect when smear metal forms is low, is cut performance and reduces.
Comparative steel 3 in toughness, hot workability, be cut on performance, anti-the getting rusty property and all demonstrated sufficient characteristic.But embodiment 2 is described as described later, and is restricted on for the heat-treat condition that obtains the hardness more than the 30HRC.
Comparative steel 4 is by the optimization of C amount, and is excellent on anti-getting rusty property.But owing to manage into high Cr amount, low Cu amount and N amount, original in addition S amount itself is low, so it is poor to be cut performance.And, for too much Ni and Al amount, because comparative example 4 is to separate out fine Ni by the mutual interpolation of Ni and Al
3Al intermetallic compound and given the metal pattern steel of hardness makes the extreme principal element that reduces of toughness so this becomes.
Comparative steel 5,6 is to have the steel of suitable composition on the main component of metal pattern with steel.But, because the Al of comparative steel 5 and N amount are too much, so formed the non-metallic inclusion Al of hard
2O
3, thick AlN, thereby toughness, hot workability, be cut performance and reduce.And,,, reduce thereby be cut performance so the breach effect the when smear metal in the machinability forms reduces because the N of comparative steel 6 amount is few.
Embodiment 2
The steel of the present invention 3 and the comparative steel 3 of table 1 are carried out quench treatment from 1030 ℃.Then, these are carried out temper in each temperature, and measure the changes in hardness that tempering temperature at this moment causes.Consequent tempering temperature curve is shown in Fig. 2.In the tempering temperature more than 550 ℃, also can stably reach hardness more than the 30HRC even be added with the steel of the present invention 3 of the C amount more than 0.1%.Relative therewith, the comparative steel 3 of C quantity not sufficient 0.1% can not stably reach the hardness of 30HRC in identical tempering temperature.
Industrial applicibility
Metal pattern of the present invention because it has excellent mechanical property and is cut performance, also can be applied to other the precision machined product that requires with steel.
Claims (6)
1. metal pattern steel that has superior hot workability, it is characterized in that, comprise: in quality %, C:0.1～less than 0.2%, Si: greater than 0～1.2%, Mn:1.2～2.0%, S:0.01～0.1%, Ni:0.5～1.5%, Cr:12.0～13.0%, Mo:0.3～0.8%, V:0.07～～0.3%, Cu:0.1～1.0%, below the Al:0.05%, N:0.03～0.1%, surplus is Fe and unavoidable impurities.
2. the metal pattern steel that has superior hot workability according to claim 1 is characterized in that, in quality %, and Si:0.1～0.8%.
3. the metal pattern steel that has superior hot workability according to claim 1 and 2 is characterized in that, in quality %, and S:0.05～0.1%.
4. according to any described metal pattern steel that has superior hot workability of claim 1 to 3, it is characterized in that, in quality %, N:0.04～0.1%.
5. according to any described metal pattern steel that has superior hot workability of claim 1 to 4, it is characterized in that, count below 0.02% with quality % as the O of unavoidable impurities.
6. according to any described metal pattern steel that has superior hot workability in the claim 1 to 5, it is characterized in that hardness is 30～45HRC.
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106062233A (en) * | 2014-01-16 | 2016-10-26 | 尤迪霍尔姆斯有限责任公司 | Stainless steel and a cutting tool body made of the stainless steel |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| JP2000144334A (en) * | 1998-11-06 | 2000-05-26 | Daido Steel Co Ltd | Steel for aluminum diecasting die excellent in erosion resistance |
| CN1723293A (en) * | 2002-12-25 | 2006-01-18 | 日立金属株式会社 | Cold die steel excellent in characteristic of suppressing dimensional change |
| CN101264681A (en) * | 2001-06-06 | 2008-09-17 | 新日本制铁株式会社 | Hot-dip galvannealed steel sheet, steel sheet treated by hot-dip galvannealed layer diffusion and a method of producing the same |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2000239805A (en) * | 1999-02-19 | 2000-09-05 | Daido Steel Co Ltd | High hardness martensitic stainless steel excellent in corrosion resistance and cold workability |
| US8808472B2 (en) * | 2000-12-11 | 2014-08-19 | Uddeholms Ab | Steel alloy, holders and holder details for plastic moulding tools, and tough hardened blanks for holders and holder details |
| JP2009242820A (en) * | 2008-03-28 | 2009-10-22 | Daido Steel Co Ltd | Steel, steel for die and die using the same |
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2010
- 2010-12-06 JP JP2010271184A patent/JP5776959B2/en active Active
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Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2000144334A (en) * | 1998-11-06 | 2000-05-26 | Daido Steel Co Ltd | Steel for aluminum diecasting die excellent in erosion resistance |
| CN101264681A (en) * | 2001-06-06 | 2008-09-17 | 新日本制铁株式会社 | Hot-dip galvannealed steel sheet, steel sheet treated by hot-dip galvannealed layer diffusion and a method of producing the same |
| CN1723293A (en) * | 2002-12-25 | 2006-01-18 | 日立金属株式会社 | Cold die steel excellent in characteristic of suppressing dimensional change |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106062233A (en) * | 2014-01-16 | 2016-10-26 | 尤迪霍尔姆斯有限责任公司 | Stainless steel and a cutting tool body made of the stainless steel |
| TWI631224B (en) * | 2014-01-16 | 2018-08-01 | 伍德赫爾恩股份有限公司 | Stainless steel and a cutting tool body made of the stainless steel |
| AU2014377770B2 (en) * | 2014-01-16 | 2018-09-20 | Uddeholms Ab | Stainless steel and a cutting tool body made of the stainless steel |
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| CN102102164B (en) | 2013-04-03 |
| JP5776959B2 (en) | 2015-09-09 |
| JP2011144449A (en) | 2011-07-28 |
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