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WO2000043555A1 - Procede de production d'aciers coules a forte teneur en carbone destines a des pieces d'usure - Google Patents

Procede de production d'aciers coules a forte teneur en carbone destines a des pieces d'usure Download PDF

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Publication number
WO2000043555A1
WO2000043555A1 PCT/BE2000/000005 BE0000005W WO0043555A1 WO 2000043555 A1 WO2000043555 A1 WO 2000043555A1 BE 0000005 W BE0000005 W BE 0000005W WO 0043555 A1 WO0043555 A1 WO 0043555A1
Authority
WO
WIPO (PCT)
Prior art keywords
carbon
steel
process according
chromium
manganese
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.)
Ceased
Application number
PCT/BE2000/000005
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English (en)
Inventor
Michel Bonnevie
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Magotteaux International SA
Original Assignee
Magotteaux International SA
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Priority claimed from US09/233,208 external-priority patent/US6221184B1/en
Application filed by Magotteaux International SA filed Critical Magotteaux International SA
Priority to AU20867/00A priority Critical patent/AU2086700A/en
Publication of WO2000043555A1 publication Critical patent/WO2000043555A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • 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
    • C22C38/36—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.7% by weight of carbon
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B02—CRUSHING, PULVERISING, OR DISINTEGRATING; PREPARATORY TREATMENT OF GRAIN FOR MILLING
    • B02C—CRUSHING, PULVERISING, OR DISINTEGRATING IN GENERAL; MILLING GRAIN
    • B02C17/00—Disintegrating by tumbling mills, i.e. mills having a container charged with the material to be disintegrated with or without special disintegrating members such as pebbles or balls
    • B02C17/18—Details
    • B02C17/20—Disintegrating members
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/84—Controlled slow cooling
    • C—CHEMISTRY; METALLURGY
    • 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
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn

Definitions

  • the present invention relates to a process for the production of high-carbon cast steels which are more particularly intended for the manufacture of wearing parts, especially grinding media such as balls.
  • low-alloy martensitic steels 0.7 to 1% carbon and alloy elements less than 1%) shaped by rolling or forging and then heat-treated in order to obtain a surface hardness of 60-65 RC
  • chromium-alloy martensitic cast iron 1.7 to 3.5% carbon and 9 to 30% chromium
  • low-alloy pearlitic white cast irons 3 to 4.2% carbon and alloy elements less than 2%) not treated and having a hardness of 45 to 55 RC, obtained by casting.
  • the object of the invention is to provide a process for the production of cast steels having improved properties and most especially to remedy the drawbacks and shortcomings of the solutions in the prior art for wearing parts (in particular the grinding media) , the composition, the shaping by casting and the post-casting cooling conditions of which make it possible to obtain a wear resistance (especially under very abrasive conditions) which is comparable to that of forged martensitic steels and chromium martensitic cast irons, but with a markedly lower cost, and is markedly superior to pearlitic cast irons for a comparable cost .
  • high-carbon steels having a composition expressed in % by weight of: carbon 0.6 to 2% manganese 0.5 to 6% chromium 1 to 6% silicon 0.4 to 1.5 % the balance being iron, with the usual impurity contents, in that they have non-equilibrium structures obtained directly after solidification.
  • the structures of these steels may consist of:
  • the carbon contents are :
  • steels of the indicated composition are subjected, after casting and complete solidification, to a cooling from a temperature of at least 900 °C at a cooling rate lying between 7.5 and
  • compositions have proved to be particularly useful for the manufacture of grinding media, in particular balls having a diameter of 100-125 mm, wherein the alloy composition of the steel is: carbon of the order of 1.3 to 1.7% manganese of the order of 3 to 4% chromium of the order of 3 to 3.5% silicon of the order of 0.4 to 1% and for the manufacture of grinding media, in particular balls having a diameter of 30-90 mm, wherein the alloy composition of the steel is: carbon of the order of 1.3 to 1.7% manganese of the order of 0.3 to 2.5% chromium of the order of 1.5 to 3% silicon of the order of 0.4 to 1%.
  • compositions have proved to be particularly useful for the manufacture of grinding media, in particular balls having a diameter of 100-125 mm, wherein the alloy composition of the steel is: carbon of the order of 1 to 1.6% manganese of the order of 4.4 to 5% chromium of the order of 3.5 to 4% silicon of the order of 0.4 to 1% and for the manufacture of grinding media, in particular balls having a diameter of 25-90 mm, wherein the alloy composition of the steel is : carbon of the order of 1 to 1.6% manganese of the order of 2.6 to 4.1% chromium of the order of 2.5 to 3.5% silicon of the order of 0.4 to 1%.
  • compositions have proved to be particularly useful for the manufacture of grinding media, in particular balls having a diameter of 60-125 mm, wherein the alloy composition of the steel is: carbon of the order of 0.6 to 1% manganese of the order of 1.1 to 1.3% chromium of the order of 3 to 3.5% silicon of the order of 0.4 to 1% and for the manufacture of grinding media, in particular balls having a diameter of 30-60 mm, wherein the alloy composition of the steel is: carbon of the order of 0.6 to 1% manganese of the order of 1.3 to 1.6% chromium of the order of 2.5 to 3% silicon of the order of 0.4 to 1%.
  • the casting operation causes the shaping of the wearing pieces, and more particularly the grinding media, directly and it can be performed using any of the conventional casting techniques known in founding (especially die casting) .
  • the non-equilibrium structures are obtained by extraction (knock-out) of the still hot casting from the casting mould and by adapting the chemical composition to the mass of the casting and to the rate of cooling (natural or preferably accelerated cooling) ' which follows extraction from the mould.
  • Figure 1 is a micro-graph of a 100 mm ball showing a structure consisting of non-equilibrium pearlite (400 x magnification) .
  • Figure 2 is a micro-graph of a 70 mm ball showing a structure consisting of non-equilibrium pearlite (400 x magnification) .
  • Figure 3 is a micro-graph of a 60 mm ball showing a structure consisting of non-equilibrium austenitic (400 x magnification) .
  • Figure 4 is a micro-graph of a 40 mm ball showing a structure consisting of non-equilibrium austenitic (400 x magnification) .
  • Figure 5 is a micro-graph of a 60 mm ball showing a structure consisting of non-equilibrium martensitic (400 x magnification) .
  • Figure 6 is a micro-graph of a 40 mm ball showing a structure consisting of non-equilibrium martensitic (1000 x magnification) .
  • a steel composition is employed that contains 1.5% of carbon, 3% of chromium, 0.8% of silicon and a variable manganese content, the balance being iron with the usual impurity contents.
  • the specific manganese and chromium contents, expressed in weight % are given in various examples, in Table I, for various ball sizes.
  • the casting is extracted from its mould at a temperature as high as possible but compatible with easy handling, preferably greater than 900 °C .
  • the casting is then cooled uniformly at a well-defined rate depending on its mass. This controlled cooling is maintained down to a temperature of 500 °C, after which the nature of the cooling is immaterial .
  • Figure 1 shows the micrograph of a 100 mm ball whose chemical composition, expressed in weight %, is:
  • the measured Rockwell hardness is 51 RC .
  • the structure is composed of fine pearlite, of 6 to 8% cementite and of less than 10% martensite.
  • Figure 2 of 400 magnification is the micrograph of a 70 mm ball having as chemical composition, expressed in weight %:
  • this casting was cooled from a temperature of 1000 °C at an average cooling rate of
  • the measured Rockwell hardness is 52 RC .
  • the structure is composed of fine pearlite, of 5 to 7% cementite and of 5 to 7% martensite.
  • the grinding media or grinding balls whose micrographs are shown in Figures 1 and 2 were subjected to wearing tests in order to check their behaviour and their properties in an industrial environment.
  • the wear resistance of the alloy of the invention was thus able to be evaluated using the technique of marked-ball testing.
  • This technique consists in introducing into an industrial mill a defined quantity of balls manufactured from the alloy according to the invention, these being beforehand set to the same weight and identified by drill-holes conjointly with balls of the same weight, which are manufactured from one or various known alloys of the prior art. After a defined operating period, the mill is stopped and the marked balls within the charge are sought. The balls are weighed and the difference in weight enables the performance characteristics of the various alloys tested to be compared. These tests are repeated several times in order to obtain a statistically valid value .
  • a first test was carried out in a mill on a particularly abrasive ore - it contains more than 70% of quartz. 100 mm diameter balls were monitored every week for 5 weeks.
  • the reference ball made of martensitic chromium- alloy cast iron, was worn away from an initial weight of 4.600 kg to 2.800 kg.
  • the relative wear resistances of the various grades of alloy are summarised below: 64 RC martensitic cast iron with 12% chromium : lx
  • a steel composition was employed that contains 1.3% of carbon, 4% of chromium and 0.8% of silicon, the balance being iron with the usual impurity contents.
  • the casting is extracted from its mould at a temperature as high as possible but compatible with easy handling, preferably greater than 900 °C.
  • the casting is then cooled uniformly at a well-defined rate depending on its mass.
  • the controlled cooling is maintained down to a temperature close to room temperature and less than 1000 °C.
  • Figure 3 of 400x magnification shows the micrograph of a 60 mm ball whose composition, expressed m weight %, is:
  • the casting was cooled from a temperature of 1000 °C down to a temperature of 500 °C at an average rate of 2.5 °C/sec, and then at an average rate of 0.75 °C/s from 500 °C to room temperature.
  • the measured Rockwell hardness is 29 RC.
  • the structure is composed of non-equilibrium austenite, of 5 to 7% of pearlite, m islands or along the gram boundaries, and of approximately 5% of carbide.
  • Figure 4 of 400 ⁇ magnification is the micro graph of a 40 mm ball having as chemical composition, expressed m weight % :
  • the measured Rockwell hardness is 25 RC .
  • the structure is composed of non-equilibrium austenite, of 2-3% of pearlite and approximately 5% of carbide.
  • a first test was carried out in a mill for grinding copper and zinc sulphide ore containing approximately 11% of quartz.
  • a steel composition which contains 0.7% of carbon, 3% of chromium and 0.8% of silicon, the manganese being variable and the balance being iron with the usual impurity contents.
  • the casting is extracted from its mould at a temperature as high as possible but compatible with easy handling, preferably greater than 900 °C.
  • the casting is then cooled uniformly at a well-defined rate depending on its mass.
  • the controlled cooling is maintained down to a temperature close to room temperature .
  • the main advantages of this heat treatment are to obtain a martensitic structure easily and for the least cost and to take advantage of the residual heat of the casting after it has been cast.
  • Figure 5 of 400 ⁇ magnification, shows the micrograph of a 60 mm ball whose composition, expressed in weight %, is:
  • the measured Rockwell hardness is 64.1 RC.
  • the structure is composed of martensite, of approximately 21M residual austenite, of less than 3% pearlite and of sparse carbides at the grain boundaries.
  • Figure 6, of lOOOx magnification, is the micrograph of a 40 mm ball having as chemical composition, expressed in weight %:
  • the measured Rockwell hardness is 64.2 RC .
  • the structure is composed of martensite and of residual austenite (approximately 20%) .
  • austenite approximately 20%
  • a second test was carried out in a mill for grinding copper ore containing 11 to 30% of quartz.
  • Martensitic chromium cast iron 67 RC - 1.40 times better than forged cast iron.
  • Table V shows how the percentage of manganese and chromium may be selected for pearlite, austenitic and martensitic steels respectively for various grinding ball diameters.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Food Science & Technology (AREA)
  • Crushing And Grinding (AREA)

Abstract

Cette invention concerne un procédé de production de pièces d'usure coulées qui se composent d'alliages d'aciers à forte teneur en carbone dont la composition est la suivante: de 0,6 à 2 % en poids de carbone; de 0,5 à 6 % en poids de manganèse; de 1 à 6 % en poids de chrome; et de 0,4 à 1,5 % en poids de silicium, le reste se composant de fer et des impuretés habituelles. Ces aciers possèdent une des structures suivantes: une structure de non-équilibre de perlite fine contenant de 1 à 1,5 % en poids de carbone et dont la dureté varie de 47 à 54 RC; une structure austénitique à forte teneur en carbone dont la dureté varie de 15 à 30 RC; et une structure martensitique à forte teneur en carbone dont la dureté varie de 60 à 65 RC. Après coulage et solidification complète, on refroidit l'acier ayant la composition susmentionnée d'une température de 900 °C ou plus à une température de 500 °C à une vitesse de refroidissement de 7,5 à 1,0 °C/seconde, puis on refroidit ledit acier d'une température de 500 °C à la température ambiante à une vitesse de refroidissement de 2 à 0,4 °C/seconde.
PCT/BE2000/000005 1999-01-19 2000-01-18 Procede de production d'aciers coules a forte teneur en carbone destines a des pieces d'usure Ceased WO2000043555A1 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
AU20867/00A AU2086700A (en) 1999-01-19 2000-01-18 Process of the production of high-carbon cast steels intended for wearing parts

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
US09/233,208 US6221184B1 (en) 1998-01-19 1999-01-19 Process of the production of high-carbon cast steels intended for wearing parts
US09/233,208 1999-01-19

Publications (1)

Publication Number Publication Date
WO2000043555A1 true WO2000043555A1 (fr) 2000-07-27

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AU (1) AU2086700A (fr)
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Cited By (20)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2826299A1 (fr) * 2001-06-25 2002-12-27 Wheelabrator Allevard Procede et dispositif de broyage fin de particules minerales
DE10348992B3 (de) * 2003-10-22 2005-06-09 Boris Turevsky Verschleißfester Stahl
CN103627990A (zh) * 2013-11-11 2014-03-12 马鞍山市恒毅机械制造有限公司 一种矿山用耐磨不锈钢锤头材料及其制备方法
CN103627978A (zh) * 2013-11-11 2014-03-12 马鞍山市恒毅机械制造有限公司 一种含铌矿山锤头用合金钢材料及其制备方法
CN103627999A (zh) * 2013-11-11 2014-03-12 马鞍山市恒毅机械制造有限公司 一种矿山用中锰钢锤头材料及其制备方法
CN103627989A (zh) * 2013-11-11 2014-03-12 马鞍山市恒毅机械制造有限公司 一种矿用破碎机锤头用合金钢材料及其制备方法
CN103627997A (zh) * 2013-11-11 2014-03-12 马鞍山市恒毅机械制造有限公司 一种高钨高碳钢锤头材料及其制备方法
CN103627985A (zh) * 2013-11-11 2014-03-12 马鞍山市恒毅机械制造有限公司 一种含钨钇矿用破碎锤头用合金钢材料及其制备方法
CN103627966A (zh) * 2013-11-11 2014-03-12 马鞍山市恒毅机械制造有限公司 一种高硬度中锰钢锤头材料及其制备方法
CN103628000A (zh) * 2013-11-11 2014-03-12 马鞍山市恒毅机械制造有限公司 一种含钨矿山锤头用合金钢材料及其制备方法
CN103627982A (zh) * 2013-11-11 2014-03-12 马鞍山市恒毅机械制造有限公司 一种高硼强耐磨锤头用合金材料及其制备方法
CN103627986A (zh) * 2013-11-11 2014-03-12 马鞍山市恒毅机械制造有限公司 一种制砂机锤头用合金钢材料及其制备方法
CN103627983A (zh) * 2013-11-11 2014-03-12 马鞍山市恒毅机械制造有限公司 一种矿用破碎锤用耐磨合金钢材料及其制备方法
CN103627965A (zh) * 2013-11-11 2014-03-12 马鞍山市恒毅机械制造有限公司 一种高硬度的合金钢锤头材料及其制备方法
CN103627988A (zh) * 2013-11-11 2014-03-12 马鞍山市恒毅机械制造有限公司 一种高硬度防断裂锤头用合金钢材料及其制备方法
CN103643162A (zh) * 2013-11-11 2014-03-19 马鞍山市恒毅机械制造有限公司 一种矿山用摆锤锤头用合金钢材料及其制备方法
CN103643112A (zh) * 2013-11-11 2014-03-19 马鞍山市恒毅机械制造有限公司 一种耐高温矿山锤头用合金材料及其制备方法
CN104056696A (zh) * 2014-06-05 2014-09-24 宁国慧宏耐磨材料有限公司 一种湿法磨矿山专用球及其加工工艺
CN114929906A (zh) * 2020-01-16 2022-08-19 曼格特奥克斯国际有限公司 用于半自体研磨机的锻造研磨球
CN118792596A (zh) * 2024-06-26 2024-10-18 广东润德利科技有限公司 一种塑料模具钢及生产工艺

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE2456137A1 (de) * 1974-11-27 1976-08-12 Commw Aircraft Corp Proprietar Manganstaehle sowie verfahren zu deren herstellung
EP0120748A1 (fr) * 1983-03-01 1984-10-03 ACIERIES THOME CROMBACK Société anonyme dite: Barre de broyage à haute résistance et son procédé de fabrication
WO1995028506A1 (fr) * 1994-04-18 1995-10-26 Magotteaux International S.A. Acier a forte teneur en carbone, son procede de fabrication, et son utilisation en tant que pieces d'usure en acier de ce type

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE2456137A1 (de) * 1974-11-27 1976-08-12 Commw Aircraft Corp Proprietar Manganstaehle sowie verfahren zu deren herstellung
EP0120748A1 (fr) * 1983-03-01 1984-10-03 ACIERIES THOME CROMBACK Société anonyme dite: Barre de broyage à haute résistance et son procédé de fabrication
WO1995028506A1 (fr) * 1994-04-18 1995-10-26 Magotteaux International S.A. Acier a forte teneur en carbone, son procede de fabrication, et son utilisation en tant que pieces d'usure en acier de ce type

Cited By (23)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2826299A1 (fr) * 2001-06-25 2002-12-27 Wheelabrator Allevard Procede et dispositif de broyage fin de particules minerales
WO2003000427A1 (fr) * 2001-06-25 2003-01-03 Wheelabrator - Allevard Procede et dispositif de broyage fin de particules minerales
US7093782B2 (en) 2001-06-25 2006-08-22 Wheelabrator-Allevard Method and device for fine grinding of mineral particles
DE10348992B3 (de) * 2003-10-22 2005-06-09 Boris Turevsky Verschleißfester Stahl
CN103627966A (zh) * 2013-11-11 2014-03-12 马鞍山市恒毅机械制造有限公司 一种高硬度中锰钢锤头材料及其制备方法
CN103627986A (zh) * 2013-11-11 2014-03-12 马鞍山市恒毅机械制造有限公司 一种制砂机锤头用合金钢材料及其制备方法
CN103627999A (zh) * 2013-11-11 2014-03-12 马鞍山市恒毅机械制造有限公司 一种矿山用中锰钢锤头材料及其制备方法
CN103627989A (zh) * 2013-11-11 2014-03-12 马鞍山市恒毅机械制造有限公司 一种矿用破碎机锤头用合金钢材料及其制备方法
CN103627997A (zh) * 2013-11-11 2014-03-12 马鞍山市恒毅机械制造有限公司 一种高钨高碳钢锤头材料及其制备方法
CN103627985A (zh) * 2013-11-11 2014-03-12 马鞍山市恒毅机械制造有限公司 一种含钨钇矿用破碎锤头用合金钢材料及其制备方法
CN103627990A (zh) * 2013-11-11 2014-03-12 马鞍山市恒毅机械制造有限公司 一种矿山用耐磨不锈钢锤头材料及其制备方法
CN103628000A (zh) * 2013-11-11 2014-03-12 马鞍山市恒毅机械制造有限公司 一种含钨矿山锤头用合金钢材料及其制备方法
CN103627982A (zh) * 2013-11-11 2014-03-12 马鞍山市恒毅机械制造有限公司 一种高硼强耐磨锤头用合金材料及其制备方法
CN103627978A (zh) * 2013-11-11 2014-03-12 马鞍山市恒毅机械制造有限公司 一种含铌矿山锤头用合金钢材料及其制备方法
CN103627983A (zh) * 2013-11-11 2014-03-12 马鞍山市恒毅机械制造有限公司 一种矿用破碎锤用耐磨合金钢材料及其制备方法
CN103627965A (zh) * 2013-11-11 2014-03-12 马鞍山市恒毅机械制造有限公司 一种高硬度的合金钢锤头材料及其制备方法
CN103627988A (zh) * 2013-11-11 2014-03-12 马鞍山市恒毅机械制造有限公司 一种高硬度防断裂锤头用合金钢材料及其制备方法
CN103643162A (zh) * 2013-11-11 2014-03-19 马鞍山市恒毅机械制造有限公司 一种矿山用摆锤锤头用合金钢材料及其制备方法
CN103643112A (zh) * 2013-11-11 2014-03-19 马鞍山市恒毅机械制造有限公司 一种耐高温矿山锤头用合金材料及其制备方法
CN104056696A (zh) * 2014-06-05 2014-09-24 宁国慧宏耐磨材料有限公司 一种湿法磨矿山专用球及其加工工艺
CN114929906A (zh) * 2020-01-16 2022-08-19 曼格特奥克斯国际有限公司 用于半自体研磨机的锻造研磨球
CN118792596A (zh) * 2024-06-26 2024-10-18 广东润德利科技有限公司 一种塑料模具钢及生产工艺
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