CA2869798A1 - Method for producing plastic molds made from martensitic chromium steel and plastic mold - Google Patents
Method for producing plastic molds made from martensitic chromium steel and plastic mold Download PDFInfo
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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- 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
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- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
- C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
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- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/0068—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for particular articles not mentioned below
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- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
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- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
- B29C—SHAPING OR JOINING OF PLASTICS; SHAPING OF MATERIAL IN A PLASTIC STATE, NOT OTHERWISE PROVIDED FOR; AFTER-TREATMENT OF THE SHAPED PRODUCTS, e.g. REPAIRING
- B29C33/00—Moulds or cores; Details thereof or accessories therefor
- B29C33/38—Moulds or cores; Details thereof or accessories therefor characterised by the material or the manufacturing process
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- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/004—Dispersions; Precipitations
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- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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- Crystallography & Structural Chemistry (AREA)
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Abstract
The invention relates to a method for producing plastic molds made of a martensitic chromium steel and it relates to a plastic mold. In order to achieve equally high quality values of the mold material, it is provided according to the invention to produce a steel block having the composition in wt% of C = 0.22 to 0.26, Si = 0.01 to 0.35, Mn = 0.15 to 0.60, P = max. 0.025, S = max. 0.003, Cr = 12.0 to 14.0, Mo = 0.10 to 0.18, Ni =0.35 to 0.50, V= 0.15 to 0.25, W = traces up to 0.20, Cu = traces up to 0.30, Co = traces up to 0.20, Ti = traces up to 0.02, Hf = traces up to 0.02, Zr = traces up to 0.02, Al = 0.002 to 0.02, Nb = traces up to 0.04, B = traces up to 0.001, N = 0.08 to 0.15, Ta = traces up to 0.04, As = traces up to 0.005, with the condition: Mn+Ni = 0.55 to 0.95, Mo+W/2 = 0.11 to 0.20, Ti+Hf-FZr = traces up to 0.008, V+Nb+Ta = 0.15 to 0.30, Nb+Ta = traces up to 0.04, Fe and contaminants = the rest, and with a PRE(N) value for the corrosion resistance from more than 14.5 to approximately 15.7, and to subject said steel block to a primary forming at a temperature of more 1050 °C with a forming degree of more than 2.5 fold, optionally after an intermediate cooling, from the blank at a temperature of less than 1050 °C, a manufacturing of at least one basic mold part occurs, from which, optionally after a machining treatment, a plastic mold is produced, and said plastic mold or the basic mold part is austenized and hardened at a cooling rate with a value .lambda. of less than 24, preceded by a tempering treatment is carried out at least twice at a temperature in the range from 510 to 550 °C, resulting in a hardness of the material from 48 to 52 HRC and a toughness thereof, measured on impact bending specimens, of at least 60 J, after which finally a final machining processing occurs, and, if provided for, a polishing of the plastic mold occurs.
Description
Method for Producing Plastic Molds Made from Martensitic Chromium Steel and Plastic Mold The invention relates to a method for producing plastic molds made from a martensitic chromium steel.
The invention further relates to a plastic mold.
Plastic molds, when used in production, undergo numerous stresses that the material must withstand in each case during long-term operation.
These stresses on the material mainly comprise corrosive chemical stresses, particularly at increased temperature due to the plastic molding compounds used, such as PVC, wearing stresses of the mold work surfaces due to abrasively acting molding compound additives as well as alternating mechanical stresses acting intermittently in the context of the respective production shots.
Moreover, a high polishing quality of the work surface of the mold is often required, in order to achieve an acceptable surface of the products.
Plastic molds having a particularly high dimensional accuracy are increasingly produced by machining from formed and thermally hardened molded bodies such as bars, blocks and the like. This starting material must have, over the entire inner cross section, the same material properties as well as the same homogeneous structure, high steel purity and the same mechanical material characteristic values.
Currently, martensitic chromium steels are used most commonly as material for plastic molds having the above requirement profile. Plastic molds have also been manufactured frequently from an alloy according to AT 407 647 and used successfully.
However, occasionally the manufacturing methods and the existing concentrations of the respective alloy elements were such that not all the desired values of the property profile of the martensitic corrosion-resistant chromium steel were fully reached in each production.
The problem of the invention then is to indicate a method for producing plastic molds of the type mentioned in the introduction, whereby in equal measure high corrosion resistance including at increased temperatures, resistance to wear of the molding work surface, high mechanical values, in particular toughness for minimizing the initiation of cracks and for ensuring manufacturing reliability, high fatigue strength and hardness, the maximum polishing quality and a fine homogeneous microstructure of the material over the entire cross section of the mold are achieved.
The problem is solved in a method according to the preamble for producing plastic molds in that a steel block is produced which has a composition in wt% of:
0.22 to 0.26 Si = 0.01 to 0.35 Mn = 0.15 to 0.60 max. 0.025 max. 0.003 Cr = 12.0 to 14.0 Mo = 0.10 to 0.18 Ni = 0.35 to 0.50 V = 0.15 to 0.25 W = traces up to 0.20 Cu traces up to 0.30 Co traces up to 0.20 Ti traces up to 0.02
The invention further relates to a plastic mold.
Plastic molds, when used in production, undergo numerous stresses that the material must withstand in each case during long-term operation.
These stresses on the material mainly comprise corrosive chemical stresses, particularly at increased temperature due to the plastic molding compounds used, such as PVC, wearing stresses of the mold work surfaces due to abrasively acting molding compound additives as well as alternating mechanical stresses acting intermittently in the context of the respective production shots.
Moreover, a high polishing quality of the work surface of the mold is often required, in order to achieve an acceptable surface of the products.
Plastic molds having a particularly high dimensional accuracy are increasingly produced by machining from formed and thermally hardened molded bodies such as bars, blocks and the like. This starting material must have, over the entire inner cross section, the same material properties as well as the same homogeneous structure, high steel purity and the same mechanical material characteristic values.
Currently, martensitic chromium steels are used most commonly as material for plastic molds having the above requirement profile. Plastic molds have also been manufactured frequently from an alloy according to AT 407 647 and used successfully.
However, occasionally the manufacturing methods and the existing concentrations of the respective alloy elements were such that not all the desired values of the property profile of the martensitic corrosion-resistant chromium steel were fully reached in each production.
The problem of the invention then is to indicate a method for producing plastic molds of the type mentioned in the introduction, whereby in equal measure high corrosion resistance including at increased temperatures, resistance to wear of the molding work surface, high mechanical values, in particular toughness for minimizing the initiation of cracks and for ensuring manufacturing reliability, high fatigue strength and hardness, the maximum polishing quality and a fine homogeneous microstructure of the material over the entire cross section of the mold are achieved.
The problem is solved in a method according to the preamble for producing plastic molds in that a steel block is produced which has a composition in wt% of:
0.22 to 0.26 Si = 0.01 to 0.35 Mn = 0.15 to 0.60 max. 0.025 max. 0.003 Cr = 12.0 to 14.0 Mo = 0.10 to 0.18 Ni = 0.35 to 0.50 V = 0.15 to 0.25 W = traces up to 0.20 Cu traces up to 0.30 Co traces up to 0.20 Ti traces up to 0.02
2 Hf traces up to 0.02 Zr traces up to 0.02 Al = 0.002 to 0.02 Nb traces up to 0.04 traces up to 0.001 0.08 to 0.15 Ta traces up to 0.04 As traces up to 0.005 with the condition:
Mn+Ni = 0.55 to 0.95 Mo+W/2 = 0.11 to 0.20 Ti+Hf+Zr traces up to 0.05 V+Nb+Ta 0.15 to 0.30 Nb+Ta traces up to 0.04 Fe and contaminating elements = the rest and a PRE(N) value for the corrosion resistance from more than 14.5 to approximately 15.7, and said steel block undergoes a primary forming at a temperature above with a forming degree of more than 2.5 fold, after which, optionally after an intermediate cooling, a production of at least one basic mold part is carried out at a temperature of less than 1050 C, from which, optionally after a machining processing, a plastic mold is produced, and said plastic mold or the basic mold part is austenitized and hardened at a cooling rate with a value A of less than 24, after which a tempering treatment repeated at least two times occurs at a temperature in the range from 510 to 550 C, resulting in the formation of a hardness of the material from 48 to 52 HRC and a toughness thereof,
Mn+Ni = 0.55 to 0.95 Mo+W/2 = 0.11 to 0.20 Ti+Hf+Zr traces up to 0.05 V+Nb+Ta 0.15 to 0.30 Nb+Ta traces up to 0.04 Fe and contaminating elements = the rest and a PRE(N) value for the corrosion resistance from more than 14.5 to approximately 15.7, and said steel block undergoes a primary forming at a temperature above with a forming degree of more than 2.5 fold, after which, optionally after an intermediate cooling, a production of at least one basic mold part is carried out at a temperature of less than 1050 C, from which, optionally after a machining processing, a plastic mold is produced, and said plastic mold or the basic mold part is austenitized and hardened at a cooling rate with a value A of less than 24, after which a tempering treatment repeated at least two times occurs at a temperature in the range from 510 to 550 C, resulting in the formation of a hardness of the material from 48 to 52 HRC and a toughness thereof,
3 measured using impact bending specimens, of at least 60 J, after which finally a final machining treatment occurs and, if provided for, a polishing of the plastic mold.
On should essentially consider the advantages achieved with the invention to be that a plastic mold produced according to the method in any case has a desired corrosion resistance even at increased temperatures and a good resistance to wear, high mechanical property values, in particular toughness of the material, and a fine uniform microstructure over the cross section with maximum polishing quality.
In order to achieve the above-mentioned advantageous material properties of the plastic mold, the composition of the steel is important, as was determined on the basis of the reaction kinetics of the elements.
Carbon within narrow limits with contents from 0.22 to 0.26 wt% and nitrogen in the concentration range from 0.08 to 0.15 wt% are the elements that in the end determine the hardness and the microstructure, wherein an advantageous carbonitride formation is achievable. Nitrogen contents higher than 0.15 wt% and in particular simultaneously carbon contents higher than 0.26 wt%, together with the carbide- and nitride-forming elements, can form coarse nitrides, carbides or carbonitrides in the structure, which, on the one hand, lower the polishability of the steel, have a negative influence on the mechanical properties, and in particular reduce the corrosion resistance, since coarse chromium-containing mixed carbides of the matrix in the surface region remove chromium or reduce the chromium content and as a result promote corrosive attack.
The respective activity of the carbide- or carbonitride-forming elements chromium, molybdenum, vanadium, tungsten, titanium, hafnium, zirconium, niobium and tantalum with their interaction with regard to the carbon and nitrogen content is, as was determined,
On should essentially consider the advantages achieved with the invention to be that a plastic mold produced according to the method in any case has a desired corrosion resistance even at increased temperatures and a good resistance to wear, high mechanical property values, in particular toughness of the material, and a fine uniform microstructure over the cross section with maximum polishing quality.
In order to achieve the above-mentioned advantageous material properties of the plastic mold, the composition of the steel is important, as was determined on the basis of the reaction kinetics of the elements.
Carbon within narrow limits with contents from 0.22 to 0.26 wt% and nitrogen in the concentration range from 0.08 to 0.15 wt% are the elements that in the end determine the hardness and the microstructure, wherein an advantageous carbonitride formation is achievable. Nitrogen contents higher than 0.15 wt% and in particular simultaneously carbon contents higher than 0.26 wt%, together with the carbide- and nitride-forming elements, can form coarse nitrides, carbides or carbonitrides in the structure, which, on the one hand, lower the polishability of the steel, have a negative influence on the mechanical properties, and in particular reduce the corrosion resistance, since coarse chromium-containing mixed carbides of the matrix in the surface region remove chromium or reduce the chromium content and as a result promote corrosive attack.
The respective activity of the carbide- or carbonitride-forming elements chromium, molybdenum, vanadium, tungsten, titanium, hafnium, zirconium, niobium and tantalum with their interaction with regard to the carbon and nitrogen content is, as was determined,
4 adjusted within the indicated ranges to the size, form and distribution of the desired reaction products. However, it is essential here that the total contents are Mo+W/2 = 0.11 to 0.20 Ti+Hf+Zr = traces up to 0.05 V+Nb+TA = 0.15 to 0.30 Nb+Ta = traces up to 0.04 each in wt%.
The above molecular formulas for some carbide formers take into account, according to the invention, the reaction kinetics and the crystal structure of the carbides.
(The values for Hf, Zr and Ta were calculated via the free enthalpy of formation of the compounds).
In the case of an austenitization of the homogenized material for a hardening, under the above concentration conditions, extensive dissolution of the Cr-Mo-W and most of the V compounds with (C and N) occurs. Only the finest mixed carbonitrides with vanadium and/or carbonitrides of Nb and/or Ta, which comprise only to the smallest extent a metal portion made of several elements, remain homogeneously distributed with a diameter in the nanometer range in the matrix, and they prevent grain growth at a given hardening temperature of less than 1050 C, which in the end is crucial for an improvement of the mechanical properties of the material of the plastic mold.
In the case of large basic mold parts, achieving a sufficient hardening depth or complete hardening in the case of a thermal aging requires concentrations of manganese of 0.15 to 0.60 and of nickel of 0.30 to 0.60, each in wt%. However, in order to control an austenite-stabilizing effect of these elements a content of (Mn + Ni) of 0.55 to 0.95 wt% is provided to be limiting according to the invention.
Since, as explained above, a coarsening of the carbonitride deposits in the structure formation is prevented, there is necessarily no noticeable enrichment of Cr on the surface thereof, which prevents corrosive attack precisely there, when the alloy has a PRE(N) value from more than 14.4 to approximately 15.7. The PREN-value is obtained from (%Cr+3.3x(YoMo+16x(YoN).
In order to disintegrate microscopic segregations in the cast piece or to promote material homogeneity, it is advantageous to carry out the forming of the rough block at a temperature of more than 1050 C with a forming degree of more than 2.5 fold.
(The forming degree is the quotient of the starting cross section over the final cross section).
In the case of a hardening of the material characterized according to the invention by its chemical composition, it is necessary to establish a martensitic microstructure over the entire cross section of the basic mold part or of the mold, so that a forced cooling of the austenite should be used for the martensite formation. Low cooling rates can possibly also produce to a small extent the formation of a perlitic structure or of an intermediate structure at the grain boundaries, which decisively worsens the toughness values of the material.
Therefore, according to the invention, a cooling rate from the austenite temperature of the steel with a value A of less than 24 should be applied. (The value A is obtained from the cooling time from 800 C to 500 C in seconds divided by 100.) A tempering of the hardened rough mold or mold, to achieve the complete conversion of the austenite, requires heating the part at least two times to a temperature in the range from 510 to 550 C, in order to establish a hardness of the material in the range from 48 to 52 HRC. According to the invention, the toughness of the material thereafter is at least 60 J, measured with an impact bending test. (According to ASTM, E23).
Preferred embodiments of the method according to the invention are characterized in Claims 2 and 3.
The invention also relates to a plastic mold with high mechanical and chemical corrosion resistance as well as high polishing quality.
The plastic mold is characterized by a chemical composition that is indicated in Claim 4, wherein Claim 5 indicates a preferred variant thereof.
A material having the above-mentioned composition, after a heat treatment, confers to the plastic mold a hardness from 48 to 52 HRC with a material toughness of at least 60 J
measured on impact bending specimens according to ASTM, E23.
Regarding the ductility of the material of the mold in the ready-to-use state, according to the invention, in the tensile test according to EN 10002-1, the elongation at rupture A is at least 5% and the necking is at least 10%.
These mechanical values are minimum values which in any case are usually exceeded even in the case of a more disadvantageous alloy situation. Toughness values of at least 190 J in the case of an elongation at rupture A of 10% and a necking Z of at least 40% are consistently achievable.
Based on results from the development studies, the invention will be explained in further detail below.
In Table 1, alloys according to the prior art and materials according to the invention are compared.
Alloy 1 corresponds to the steel AISI 420 or X42Cr13, materials which are frequently used as mold in the case of chemically aggressive molding compounds with abrading additives.
As additional alloy 2 pertaining to the prior art, a material according to EP
was examined.
Alloy 3 is also part of the prior art, and it has a high capacity to harden completely.
Alloy 4 and alloy 5 are microalloyed materials according to the invention for plastic molds.
Using micrographs, the effect of the added microalloy elements according to the invention, V and Nb is illustrated.
Figure 1 and Figure 2 show the structure of alloy 2 with coarse grain (ASTM 5) and perlite or intermediate stage areas at the grain boundaries, which worsen the mechanical properties of the material to a considerable extent.
On the other hand, Figure 3 and Figure 4 show the fine microstructure with an ASTM grain size from 8 to 10 of the alloys 4 and 5 according to the invention.
The impact bending study of unnotched specimens of the material depends on the austenization temperature of the cooling, the cooling rate and the tempering conditions.
To distinguish between alloy 2 and ?Hoy 5 according to the invention, the same tempering conditions were selected.
In Figure 5, the measurement results of the investigated alloys are compared, wherein a clear improvement of the toughness of the material with decreasing hardening temperature was determined.
A comparison of the elongation at rupture and the necking at rupture in the tensile test of alloy 2 and alloy 4 according to the invention is shown in Figure 6.
During the hardening of the samples, a cooling at a rate of A = 20 occurred.
The low values of alloy 2 are explained by a formation of perlite phases at the grain boundaries, as is particularly apparent in Figure 2.
Alloy C Si Mn Cr Mo. I Ni 1 V Nb 1 N i Ai W i Ti ! Hf I Zr I Ta I
1 _ 0,38 0.68 ! 0,29 14,31 0,0S' 0,21 0.20 1 <0,0051 0,02 0,006 n.d. 1 n.d. - ; -I
2 0,28 0,28 1 0,26 13,45 0,06 0.18 0.03 i <0.005! 0,10 1 0.01 , 0.01 i 0,05 j 1 - ! -3 ' 0,26 0,39 li 0.56 13.28 0.43 1 1,33 0,35 l<0.0051 0.13 j 0.009 0,11 1 n.d. - -4 1 0,26 0,21 I 0.35 13.29 ! 0.18 1 0.39 0.18 1 0.038 ! 0,10 0,008 I <0,01 1 0,001 - I -) 0,25 0,31 ! 0,41 I 13,151 0,11 i 0,28 0,21 j <0.005!
0.12 L0.007 I 0,04 ! 0.064 ' -Tab.]
Alloy Mn+Ni I Mo+Wr2 Ti+Ht+Zr 1 V+Nb+Ta I
1 , 0.5 . 0,09 - i 0.2 2 0,44 ! 0.065 0.05 i 0.03 ., 3 ' 1,89 ! 0.485 : - 1 0,35 4 ' 0,74 ! 0.185 1 0,001 ,, 0,218
The above molecular formulas for some carbide formers take into account, according to the invention, the reaction kinetics and the crystal structure of the carbides.
(The values for Hf, Zr and Ta were calculated via the free enthalpy of formation of the compounds).
In the case of an austenitization of the homogenized material for a hardening, under the above concentration conditions, extensive dissolution of the Cr-Mo-W and most of the V compounds with (C and N) occurs. Only the finest mixed carbonitrides with vanadium and/or carbonitrides of Nb and/or Ta, which comprise only to the smallest extent a metal portion made of several elements, remain homogeneously distributed with a diameter in the nanometer range in the matrix, and they prevent grain growth at a given hardening temperature of less than 1050 C, which in the end is crucial for an improvement of the mechanical properties of the material of the plastic mold.
In the case of large basic mold parts, achieving a sufficient hardening depth or complete hardening in the case of a thermal aging requires concentrations of manganese of 0.15 to 0.60 and of nickel of 0.30 to 0.60, each in wt%. However, in order to control an austenite-stabilizing effect of these elements a content of (Mn + Ni) of 0.55 to 0.95 wt% is provided to be limiting according to the invention.
Since, as explained above, a coarsening of the carbonitride deposits in the structure formation is prevented, there is necessarily no noticeable enrichment of Cr on the surface thereof, which prevents corrosive attack precisely there, when the alloy has a PRE(N) value from more than 14.4 to approximately 15.7. The PREN-value is obtained from (%Cr+3.3x(YoMo+16x(YoN).
In order to disintegrate microscopic segregations in the cast piece or to promote material homogeneity, it is advantageous to carry out the forming of the rough block at a temperature of more than 1050 C with a forming degree of more than 2.5 fold.
(The forming degree is the quotient of the starting cross section over the final cross section).
In the case of a hardening of the material characterized according to the invention by its chemical composition, it is necessary to establish a martensitic microstructure over the entire cross section of the basic mold part or of the mold, so that a forced cooling of the austenite should be used for the martensite formation. Low cooling rates can possibly also produce to a small extent the formation of a perlitic structure or of an intermediate structure at the grain boundaries, which decisively worsens the toughness values of the material.
Therefore, according to the invention, a cooling rate from the austenite temperature of the steel with a value A of less than 24 should be applied. (The value A is obtained from the cooling time from 800 C to 500 C in seconds divided by 100.) A tempering of the hardened rough mold or mold, to achieve the complete conversion of the austenite, requires heating the part at least two times to a temperature in the range from 510 to 550 C, in order to establish a hardness of the material in the range from 48 to 52 HRC. According to the invention, the toughness of the material thereafter is at least 60 J, measured with an impact bending test. (According to ASTM, E23).
Preferred embodiments of the method according to the invention are characterized in Claims 2 and 3.
The invention also relates to a plastic mold with high mechanical and chemical corrosion resistance as well as high polishing quality.
The plastic mold is characterized by a chemical composition that is indicated in Claim 4, wherein Claim 5 indicates a preferred variant thereof.
A material having the above-mentioned composition, after a heat treatment, confers to the plastic mold a hardness from 48 to 52 HRC with a material toughness of at least 60 J
measured on impact bending specimens according to ASTM, E23.
Regarding the ductility of the material of the mold in the ready-to-use state, according to the invention, in the tensile test according to EN 10002-1, the elongation at rupture A is at least 5% and the necking is at least 10%.
These mechanical values are minimum values which in any case are usually exceeded even in the case of a more disadvantageous alloy situation. Toughness values of at least 190 J in the case of an elongation at rupture A of 10% and a necking Z of at least 40% are consistently achievable.
Based on results from the development studies, the invention will be explained in further detail below.
In Table 1, alloys according to the prior art and materials according to the invention are compared.
Alloy 1 corresponds to the steel AISI 420 or X42Cr13, materials which are frequently used as mold in the case of chemically aggressive molding compounds with abrading additives.
As additional alloy 2 pertaining to the prior art, a material according to EP
was examined.
Alloy 3 is also part of the prior art, and it has a high capacity to harden completely.
Alloy 4 and alloy 5 are microalloyed materials according to the invention for plastic molds.
Using micrographs, the effect of the added microalloy elements according to the invention, V and Nb is illustrated.
Figure 1 and Figure 2 show the structure of alloy 2 with coarse grain (ASTM 5) and perlite or intermediate stage areas at the grain boundaries, which worsen the mechanical properties of the material to a considerable extent.
On the other hand, Figure 3 and Figure 4 show the fine microstructure with an ASTM grain size from 8 to 10 of the alloys 4 and 5 according to the invention.
The impact bending study of unnotched specimens of the material depends on the austenization temperature of the cooling, the cooling rate and the tempering conditions.
To distinguish between alloy 2 and ?Hoy 5 according to the invention, the same tempering conditions were selected.
In Figure 5, the measurement results of the investigated alloys are compared, wherein a clear improvement of the toughness of the material with decreasing hardening temperature was determined.
A comparison of the elongation at rupture and the necking at rupture in the tensile test of alloy 2 and alloy 4 according to the invention is shown in Figure 6.
During the hardening of the samples, a cooling at a rate of A = 20 occurred.
The low values of alloy 2 are explained by a formation of perlite phases at the grain boundaries, as is particularly apparent in Figure 2.
Alloy C Si Mn Cr Mo. I Ni 1 V Nb 1 N i Ai W i Ti ! Hf I Zr I Ta I
1 _ 0,38 0.68 ! 0,29 14,31 0,0S' 0,21 0.20 1 <0,0051 0,02 0,006 n.d. 1 n.d. - ; -I
2 0,28 0,28 1 0,26 13,45 0,06 0.18 0.03 i <0.005! 0,10 1 0.01 , 0.01 i 0,05 j 1 - ! -3 ' 0,26 0,39 li 0.56 13.28 0.43 1 1,33 0,35 l<0.0051 0.13 j 0.009 0,11 1 n.d. - -4 1 0,26 0,21 I 0.35 13.29 ! 0.18 1 0.39 0.18 1 0.038 ! 0,10 0,008 I <0,01 1 0,001 - I -) 0,25 0,31 ! 0,41 I 13,151 0,11 i 0,28 0,21 j <0.005!
0.12 L0.007 I 0,04 ! 0.064 ' -Tab.]
Alloy Mn+Ni I Mo+Wr2 Ti+Ht+Zr 1 V+Nb+Ta I
1 , 0.5 . 0,09 - i 0.2 2 0,44 ! 0.065 0.05 i 0.03 ., 3 ' 1,89 ! 0.485 : - 1 0,35 4 ' 0,74 ! 0.185 1 0,001 ,, 0,218
5 !,_ 0,77 i 0,17 i 0.004 I 0.186 Tat. 2
Claims (6)
1. Method for producing plastic molds each having high mechanical and chemical corrosion resistance as well as high polishing quality, wherein a steel block is produced which has a composition in wt% of:
C = 0.22 to 0.26 Si = 0.01 to 0.35 Mn = 0.15 to 0.60 P = max. 0.025 S = max. 0.003 Cr = 12.00 to 14.00 Mo = 0.10 to 0.18 Ni = 0.35 to 0.50 V = 0.15 to 0.25 W = traces up to 0.20 Cu = traces up to 0.30 Co = traces up to 0.20 Ti = traces up to 0.02 Hf = traces up to 0.02 Zr = traces up to 0.02 Al = 0.002 to 0.02 Nb = traces up to 0.04 B = traces up to 0.001 N = 0.08 to 0.15 Ta = traces up to 0.04 As = traces up to 0.005 with the condition:
Mn+Ni = 0.55 to 0.95 Mo+W/2 = 0.11 to 0.20 Ti+Hf+Zr traces up to 0.05 V+Nb+Ta 0.15 to 0.30 Nb+Ta traces up to 0.04 Fe and contaminating elements = the rest and a PRE(N) value for the corrosion resistance from more than 14.5 to approximately 15.7, and said steel block undergoes a primary forming at a temperature above 1050 °C
with a forming degree of more than 2.5 fold, after which, optionally after an intermediate cooling, a production of at least one basic mold part is carried out at a temperature of less than 1050 °C, from which, optionally after a machining processing, a plastic mold is produced, and said plastic mold or the basic mold part is austenitized and hardened at a cooling rate with a value .lambda. of less than 24, after which a tempering treatment repeated at least two times occurs at a temperature in the range from 510 to 550 °C, resulting in the formation of a hardness of the material from 48 to 52 HRC and a toughness thereof, measured using impact bending specimens, of at least 60 J, after which finally a final machining treatment occurs and, if provided for, a polishing of the plastic mold.
C = 0.22 to 0.26 Si = 0.01 to 0.35 Mn = 0.15 to 0.60 P = max. 0.025 S = max. 0.003 Cr = 12.00 to 14.00 Mo = 0.10 to 0.18 Ni = 0.35 to 0.50 V = 0.15 to 0.25 W = traces up to 0.20 Cu = traces up to 0.30 Co = traces up to 0.20 Ti = traces up to 0.02 Hf = traces up to 0.02 Zr = traces up to 0.02 Al = 0.002 to 0.02 Nb = traces up to 0.04 B = traces up to 0.001 N = 0.08 to 0.15 Ta = traces up to 0.04 As = traces up to 0.005 with the condition:
Mn+Ni = 0.55 to 0.95 Mo+W/2 = 0.11 to 0.20 Ti+Hf+Zr traces up to 0.05 V+Nb+Ta 0.15 to 0.30 Nb+Ta traces up to 0.04 Fe and contaminating elements = the rest and a PRE(N) value for the corrosion resistance from more than 14.5 to approximately 15.7, and said steel block undergoes a primary forming at a temperature above 1050 °C
with a forming degree of more than 2.5 fold, after which, optionally after an intermediate cooling, a production of at least one basic mold part is carried out at a temperature of less than 1050 °C, from which, optionally after a machining processing, a plastic mold is produced, and said plastic mold or the basic mold part is austenitized and hardened at a cooling rate with a value .lambda. of less than 24, after which a tempering treatment repeated at least two times occurs at a temperature in the range from 510 to 550 °C, resulting in the formation of a hardness of the material from 48 to 52 HRC and a toughness thereof, measured using impact bending specimens, of at least 60 J, after which finally a final machining treatment occurs and, if provided for, a polishing of the plastic mold.
2. Method for producing plastic molds according to Claim 1, wherein a steel block has a composition in wt% of 0.23 to 0.25 Si = 0.20 to 0.30 Mn = 0.32 to less than 0.5 P = max. 0.022 S = max. 0.0008 Cr = 13.00 to 13.60 Mo = 0.12 to 0.16 Ni = 0.38 to 0.48 V = 0.18 to 0.21 W = traces up to 0.20 Cu = traces up to 0.30 Co = traces up to 0.20 Ti = traces up to 0.008 Hf = traces up to 0.02 Zr = traces up to 0.02 Al = 0.006 to 0.018 Nb = traces up to 0.03 B = traces up to 0.001 N = 0.10 to 0.13 Ta = traces up to 0.04 As = traces up to 0.005 with the condition:
N+Ni = 0.50 to 0.9 Mo+W/2 = 0.14 to 0.18 Ti+Hf+Zr = traces up to 0.006 V+Nb+Ta = 0.18 to 0.25 Nb+Ta = 0.005 to 0.03 Fe and contamination elements = the rest.
N+Ni = 0.50 to 0.9 Mo+W/2 = 0.14 to 0.18 Ti+Hf+Zr = traces up to 0.006 V+Nb+Ta = 0.18 to 0.25 Nb+Ta = 0.005 to 0.03 Fe and contamination elements = the rest.
3. Method for producing plastic molds according to Claim 1 or 2, wherein, after the machining processing, the plastic mold is austenitized a temperature from 965 to 995 °C
and hardened at a cooling rate with a value .lambda. of 20 or less, after which a tempering treatment occurs, resulting in the formation of a hardness of the material of more than 48 HRC but less than 50 HRC (< 50 HRC) and a toughness of same of less than 190 J.
and hardened at a cooling rate with a value .lambda. of 20 or less, after which a tempering treatment occurs, resulting in the formation of a hardness of the material of more than 48 HRC but less than 50 HRC (< 50 HRC) and a toughness of same of less than 190 J.
4. A plastic mold with high mechanical and chemical corrosion resistance as well as high polishing quality, formed from a shaped alloy with a composition in wt%
of C = 0.22 to 0.26 Si = 0.01 to 0.35 Mn = 0.15 to 0.60 P = max. 0.025 S = max. 0.003 Cr = 12.00 to 14.00 Mo = 0.10 to 0.18 Ni = 0.35 to 0.50 V = 0.15 to 0.25 W = traces up to 0.20 Cu = traces up to 0.30 Co = traces up to 0.20 Ti = traces up to 0.02 Hf = traces up to 0.02 Zr = traces up to 0.02 Al = 0.002 to 0.02 Nb = traces up to 0.04 B = traces up to 0.001 N = 0.08 to 0.15 Ta = traces up to 0.04 As = traces up to 0.005 with the condition:
Mn+Ni = 0.55 to 0.95 Mo+W/2 = 0.11 to 0.20 Ti+Hf+Zr = traces up to 0.05 V+Nb+Ta = 0.15 to 0.30 Nb+Ta = traces up to 0.04 Fe and contamination elements = the rest, wherein the material has a hardness between 48 HRC and 52 HRC, a toughness measured on impact bending specimens of at least 60 J and a ductility with an elongation at rupture A of at least 5% in the case of a necking Z of at least 10%, and the PRE(N) value for the corrosion resistance is more than 14.5 to approximately 15.7.
of C = 0.22 to 0.26 Si = 0.01 to 0.35 Mn = 0.15 to 0.60 P = max. 0.025 S = max. 0.003 Cr = 12.00 to 14.00 Mo = 0.10 to 0.18 Ni = 0.35 to 0.50 V = 0.15 to 0.25 W = traces up to 0.20 Cu = traces up to 0.30 Co = traces up to 0.20 Ti = traces up to 0.02 Hf = traces up to 0.02 Zr = traces up to 0.02 Al = 0.002 to 0.02 Nb = traces up to 0.04 B = traces up to 0.001 N = 0.08 to 0.15 Ta = traces up to 0.04 As = traces up to 0.005 with the condition:
Mn+Ni = 0.55 to 0.95 Mo+W/2 = 0.11 to 0.20 Ti+Hf+Zr = traces up to 0.05 V+Nb+Ta = 0.15 to 0.30 Nb+Ta = traces up to 0.04 Fe and contamination elements = the rest, wherein the material has a hardness between 48 HRC and 52 HRC, a toughness measured on impact bending specimens of at least 60 J and a ductility with an elongation at rupture A of at least 5% in the case of a necking Z of at least 10%, and the PRE(N) value for the corrosion resistance is more than 14.5 to approximately 15.7.
5. Plastic mold according to Claim 3 made of an alloy having a composition in wt%
of C = 0.23 to 0.25 Si = 0.20 to 0.30 Mn = 0.32 to less than 0.5 P = max. 0.022 S = max. 0.0008 Cr = 13.00 to 13.60 Mo = 0.12 to 0.16 Ni = 0.35 to 0.48 V = 0.18 to 0.21 W = traces up to 0.20 Cu = traces up to 0.30 Co = traces up to 0.20 Ti = traces up to 0.008 Hf = traces up to 0.02 Zr = traces up to 0.02 Al = 0.006 to 0.018 Nb = traces up to 0.03 B = traces up to 0.001 N = 0.10 to 0.13 Ta = traces up to 0.04 As = traces up to 0.005 with the condition:
Mn+Ni = 0.50 to 0.90 Mo+W/2 = 0.14 to 0.18 Ti+Hf+Zr = traces up to 0.006 V+Nb+Ta = 0.18 to 0.25 Nb+Ta = 0.005 to 0.03 Fe and contamination elements = the rest.
of C = 0.23 to 0.25 Si = 0.20 to 0.30 Mn = 0.32 to less than 0.5 P = max. 0.022 S = max. 0.0008 Cr = 13.00 to 13.60 Mo = 0.12 to 0.16 Ni = 0.35 to 0.48 V = 0.18 to 0.21 W = traces up to 0.20 Cu = traces up to 0.30 Co = traces up to 0.20 Ti = traces up to 0.008 Hf = traces up to 0.02 Zr = traces up to 0.02 Al = 0.006 to 0.018 Nb = traces up to 0.03 B = traces up to 0.001 N = 0.10 to 0.13 Ta = traces up to 0.04 As = traces up to 0.005 with the condition:
Mn+Ni = 0.50 to 0.90 Mo+W/2 = 0.14 to 0.18 Ti+Hf+Zr = traces up to 0.006 V+Nb+Ta = 0.18 to 0.25 Nb+Ta = 0.005 to 0.03 Fe and contamination elements = the rest.
6. Plastic mold according to Claim 4 or 5, wherein the material has a hardness of more than 48 HRC but less than 50 HRC, a toughness of at least 190 J, and a ductility with an elongation at rupture A of 10%, in the case of a necking Z of at least 40%.
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| ATA50774/2013 | 2013-11-21 | ||
| ATA50774/2013A AT515157B1 (en) | 2013-11-21 | 2013-11-21 | Process for producing plastic molds from martensitic chromium steel and plastic mold |
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| WO2017182896A1 (en) * | 2016-04-22 | 2017-10-26 | Aperam | A process for manufacturing a martensitic stainless steel part from a sheet |
| US10508327B2 (en) | 2016-03-11 | 2019-12-17 | Daido Steel Co., Ltd. | Mold steel and mold |
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| KR102279421B1 (en) | 2017-06-30 | 2021-07-20 | 아뻬랑 | Spot welding method of martensitic stainless steel sheet |
| CN110273112A (en) * | 2018-03-16 | 2019-09-24 | 天津普信模具有限公司 | A kind of high-strength durable automobile die material and preparation method thereof |
| CN108467999B (en) * | 2018-04-27 | 2019-10-29 | 天长市协正塑业有限公司 | A kind of high tougness die steel for plastics and its production method |
| CN108866444B (en) * | 2018-07-26 | 2021-01-26 | 攀钢集团攀枝花钢铁研究院有限公司 | Corrosion-resistant mirror surface die steel and preparation method thereof |
| CN110541124B (en) * | 2019-09-10 | 2021-05-25 | 成都先进金属材料产业技术研究院有限公司 | Nitrogenous plastic die steel slab and process method thereof |
| CN111321345B (en) * | 2020-03-05 | 2021-11-16 | 中国石油天然气集团有限公司 | Tempering type high-quality continuous pipe and manufacturing method thereof |
| CN113217603B (en) * | 2021-04-30 | 2023-02-24 | 四川固锐德科技有限公司 | Cylindrical wheel for heavy-load vehicle main reducing system and preparation method thereof |
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| US6045633A (en) * | 1997-05-16 | 2000-04-04 | Edro Engineering, Inc. | Steel holder block for plastic molding |
| DE19821797C1 (en) * | 1998-05-15 | 1999-07-08 | Skf Gmbh | Hardened steel parts used for roller bearing parts |
| AT407647B (en) | 1999-05-10 | 2001-05-25 | Boehler Edelstahl | MARTENSITIC CORROSION RESISTANT CHROME STEEL |
| SE516622C2 (en) * | 2000-06-15 | 2002-02-05 | Uddeholm Tooling Ab | Steel alloy, plastic forming tool and toughened plastic forming tool |
| AT409636B9 (en) * | 2001-02-14 | 2002-12-27 | Boehler Edelstahl Gmbh & Co Kg | STEEL FOR PLASTIC MOLDS AND METHOD FOR HEAT TREATING THE SAME |
| FR2838138B1 (en) | 2002-04-03 | 2005-04-22 | Usinor | STEEL FOR THE MANUFACTURE OF PLASTIC INJECTION MOLDS OR FOR THE MANUFACTURE OF WORKPIECES FOR METAL WORKING |
| JP4624783B2 (en) * | 2002-06-13 | 2011-02-02 | ウッデホルムス アーベー | Molding tool for steel and plastic materials made of this steel |
| FR2847272B1 (en) * | 2002-11-19 | 2004-12-24 | Usinor | METHOD FOR MANUFACTURING AN ABRASION RESISTANT STEEL SHEET AND OBTAINED SHEET |
| SE526249C2 (en) | 2003-12-05 | 2005-08-02 | Erasteel Kloster Ab | Steel material and use of this material |
| JP2007009321A (en) * | 2005-06-02 | 2007-01-18 | Daido Steel Co Ltd | Steel for plastic molding die |
| JP4952888B2 (en) * | 2006-04-07 | 2012-06-13 | 大同特殊鋼株式会社 | Martensite steel |
| US20080073006A1 (en) * | 2006-09-27 | 2008-03-27 | Henn Eric D | Low alloy steel plastic injection mold base plate, method of manufacture and use thereof |
| FR2920784B1 (en) * | 2007-09-10 | 2010-12-10 | Aubert & Duval Sa | MARTENSITIC STAINLESS STEEL, PROCESS FOR MANUFACTURING WORKPIECES PRODUCED IN THIS STEEL AND PARTS PRODUCED THEREBY |
| JP5904409B2 (en) * | 2011-09-28 | 2016-04-13 | 日立金属株式会社 | Manufacturing method of steel materials for molds with excellent toughness |
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| US10508327B2 (en) | 2016-03-11 | 2019-12-17 | Daido Steel Co., Ltd. | Mold steel and mold |
| WO2017182896A1 (en) * | 2016-04-22 | 2017-10-26 | Aperam | A process for manufacturing a martensitic stainless steel part from a sheet |
| US11001916B2 (en) | 2016-04-22 | 2021-05-11 | Aperam | Method for manufacturing a martensitic stainless steel part from a sheet |
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| HUE037406T2 (en) | 2018-08-28 |
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| SI2875926T1 (en) | 2018-08-31 |
| JP6122415B2 (en) | 2017-04-26 |
| KR101718871B1 (en) | 2017-03-22 |
| CN104651745A (en) | 2015-05-27 |
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| TR201806922T4 (en) | 2018-06-21 |
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