US20130243639A1 - Tool steel for extrusion - Google Patents

Tool steel for extrusion Download PDF

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Publication number
US20130243639A1
US20130243639A1 US13/583,288 US201113583288A US2013243639A1 US 20130243639 A1 US20130243639 A1 US 20130243639A1 US 201113583288 A US201113583288 A US 201113583288A US 2013243639 A1 US2013243639 A1 US 2013243639A1
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Prior art keywords
steel
extrusion
content
tools
hardness
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US13/583,288
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Inventor
Celso Antonio Barbosa
Rafael Agnelli Mesquita
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Villares Metals SA
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Villares Metals SA
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Assigned to VILLARES METALS S/A reassignment VILLARES METALS S/A ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: BARBOSA, CELSO ANTONIO, MESQUITA, RAFAEL AGNELLI
Publication of US20130243639A1 publication Critical patent/US20130243639A1/en
Abandoned legal-status Critical Current

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    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C22C38/40—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
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/02—Making ferrous alloys by powder metallurgy

Definitions

  • the present invention relates to a steel intended for use in various hot form tools and dies, particularly for extrusion of aluminum alloys or other non-ferrous metals.
  • the material can also be employed in other hot forming processes, in which the metal to be formed withstands temperatures above 600° C., although the said steel can be employed in processes at lower temperatures or even at ambient temperature.
  • the composition of the steel in question allows it to be classified as hot work tool steel, whose primary characteristic the lower content of high-cost alloying elements, such as molybdenum and vanadium, but with tempering resistance (or resistance to loss of hardness) greater than that of conventional steels of prior art concept.
  • An additional alternative to the steel of the present invention is provided to increase hardness after nitriding, and may result in performance levels even greater than those of conventional steels, at the same time that the cost is kept low due to a simpler chemical composition.
  • Such an effect is possible by carefully designing the alloy, and setting the optimum ranges of the elements: carbon, chromium, molybdenum and aluminum.
  • hot work tools is applied to a large number of hot-forming operations, employed in industries and focused on the production of parts for mechanical applications, especially automotive parts.
  • the most popular hot-forming processes are forging of steel, and the extrusion or casting of non-ferrous alloys.
  • Other applications performed at high temperature, typically above 500/600° C. can also be classified as hot work.
  • molds, dies, punches, inserts and other forming devices are classified by the generic term: hot work tools. These tools are usually made of steels, which require special properties to withstand high temperatures and the mechanical efforts of the processes in which those tools are employed.
  • tempering resistance resistance after high temperature tempering
  • tempering resistance resistance to the loss of hardness
  • toughness the hardenability
  • physical properties such as thermal conductivity and specific heat.
  • the extrusion dies used for non-ferrous alloys, especially aluminum alloys are main hot work target for applying the steel of the present invention.
  • These typical dies comprise an important segment of the tool steel market both in Brazil and abroad.
  • the steels are very standardized, based on steels such as ABNT H13 (see Table 1), with quality requirements not as strict as those of other applications, e.g., pressure die casting, but with emphasis on lower production costs.
  • Low-alloy steels have been employed, such as DIN 1.2714 (chemical composition given in Table 1). However, their low wear resistance due to reduced hot strength and lower post-nitriding hardness prevents them from being applied.
  • a third problem of invention US 2009/0191086 relates to the hardness of the die core, which may be lower due to decreased hardenability as a result of reduced Cr and Mo contents.
  • the alloys of invention US 2009/0191086 have higher Mn content, which lead to higher hardenability, potential segregation problems (banding) and excessive austenite retention. Both effects may impair the final hardness and toughness and, thus, the tool life.
  • a final aspect can also be mentioned, with regard to the high Mn content: Scrap from this steel can hardly be incorporated into the production of conventional, low-Mn-content hot work steels.
  • invention US 2009/0191086 is considered by the authors as a cost-reducing solution, but with inferior properties.
  • the authors quantify the expected efficiency loss, of about 20 to 30% lower than that of steel H13.
  • this efficiency loss can be considered quite significant, thus requiring a reduction of the cost of the material by more than 30% to compensate the substitution.
  • a 30% lower life can only be viable if the cost of the new material is half the cost of the conventional material. From 2005 to 2008, when the cost of raw materials peaked, this could be true (though still difficult to occur, because the cost difference required is too high).
  • cost reduction can hardly be achieved for steel H13, considering only the reduction of the Mo and Cr contents.
  • reduction in cost associated with efficiency loss of the alloy of patent US 2009/0191086 can be currently considered impractical for such application.
  • the steel of the present invention has a composition of alloying elements, which, in percentage by mass consists of:
  • Al can be added simultaneously to the alloys of the present invention to provide gains in terms of hardness after nitriding, but also negative effects in terms of toughness and complexity of the steel-making process.
  • the Al content must be dosed as follows, in percentage by mass:
  • compositions should be characterized by balance by Fe (iron) and metallic or non-metallic deleterious substances inevitable to the steelmaking process, in which said non-metallic deleterious substances include but are not limited to the following elements, in percentage by mass:
  • Max 0.030 P preferably max 0.015 P, typically max 0.010 P.
  • Max 0.10 S preferably max 0.030 S, typically max 0.008 S.
  • Max 1.5 Ni or Co preferably up to 1.0 Ni or Co, typically below 0.5 Ni and Co.
  • Carbon is primarily responsible for martensite hardening under low temperature conditions. However, together with the alloying elements, carbon also plays a role in the secondary hardening, important for the hardening at high temperature. In these cases, the C content is more important for hardness at temperatures below 600° C., when hardness still depends on the martensite hardness or formation of cementite or Cr carbides. Furthermore, carbon is an important hardenability-promoting element, and causes no increase in cost. It is also considered important to increase hardness to 45 HRC and up, carbon contents of at least 0.40% are recommended, preferably above 0.45%.
  • the C content should be limited to a maximum value of 0.60%, preferably below 0.55%. This limitation also plays a role in the reduction of the amount of retained austenite, preventing problems associated with dimensional instability and embrittlement.
  • the chromium content should be higher than 2.5%, preferably greater than 3.0%, because this element favors hardenability, which is important for application in large tools.
  • the Cr content should be limited.
  • the present invention has incorporated the concept of reducing the Cr content to improve tempering resistance.
  • the mechanisms of this effect are not fully understood but they may be related to the formation of secondary Cr carbides, M 7 C 3 -type, which dissolve Mo and V are the first carbides to be formed. Therefore, the lower the Cr content, the lower the amount of M 7 C 3 carbides and, thus, the greater the amount of Mo and V available for the formation of fine carbides M 2 C and MC, which are also important for secondary hardening.
  • the end result is a significantly higher tempering resistance in steels with lower Cr content, thus enabling the reduction of the Mo content when compared to steels of prior art concept.
  • Si silicon produces a strong effect on secondary hardening and toughness.
  • toughness improves due to a better distribution of secondary carbides. Therefore, the Si content of the material of the present invention must be lower than 1.0%, typically below 0.5%.
  • Mn high Mn contents may be considered undesirable for promoting intense micro-segregation generating banding at different degrees of hardness, and for increasing the retained austenite content; therefore Mn is considered a deleterious element in the present invention.
  • the Mn content should be limited to 1.0%, preferably below 0.8%, typically below 0.50%.
  • the alloys' Al content can be high.
  • the Al content, under these conditions, should be limited to 1.0% because they lead to decreased toughness.
  • Al contents between 0.40% and 0.60% may be of interest for this purpose.
  • the Al content of the alloy of the present invention can be ⁇ 0.1%, typically below 0.05%.
  • Residual Elements Other elements such as Ni and Co should be considered as deleterious substances associated with the steelmaking deoxidation processes or inherent to the manufacturing processes. Hence, the Ni and Co content should be limited to 1.5%, preferably below 1.0%. In terms of formation of inclusions, the sulfur content should be controlled, because such inclusions may lead to cracking during operation; therefore the S content should remain below 0.050%, preferably below 0.020%. Also, for high toughness purposes, embrittling elements such as P should be avoided, being desirable P ⁇ 0.030%, preferably P ⁇ 0.015%, typically P ⁇ 0.010%. Indeed, a low Cr content also helps to reduce the P content in electric arc furnace steelmaking processes, thus leading to conclusions that are not contradictory to the cost reduction philosophy desired.
  • the alloy as described above, can be produced as rolled or forged products through conventional or special processes such as powder metallurgy, spray forming or continuous casting, such as wire rods, bars, wires, sheets and strips.
  • FIG. 1A shows the effect of the Mo content on hardness after tempering at 600° C.
  • FIGS. 1B and 1C show the effect of the Cr content at 0.60% Mo on usual C contents ( FIG. 1B ) and higher C contents ( FIG. 1C );
  • the horizontal dashed line of FIGS. 1A , 1 B and 1 C indicates the Minimum Hardness desirable for the application.
  • FIGS. 2A , 2 B and 2 C show the effect of molybdenum ( FIG. 2A ) and chromium ( FIG. 2B and FIG. 2C ) on tempering resistance.
  • FIGS. 3A and 3B show the OCT curve of the compositions of the present invention, considering two Cr contents. Quantitative hardenability results can be obtained from the number of formed phases (pearlite and bainite) and, most importantly, from the final hardness obtained per rate.
  • the compositions are summarized in Table 1, base 3, considering Cr contents of 3% and 4% for comparison purposes.
  • FIG. 3A illustrates the CCT curve for a 0.50% C, 3.00% Cr composition
  • FIG. 3B shows the CCT curve for a 0.50% C, 4.00% Cr composition.
  • FIG. 4 shows the CCT curve of H13 steel of the prior art concept, whose data can be compared to the results of the steel of the present invention.
  • the same data concerning number of phases and hardness shown in FIG. 3 can be assessed for different cooling rates.
  • FIGS. 5A and 5B the alloys with the final composition of the present invention, PI 1 to PI 3, are compared in terms of hardness after tempering ( FIG. 5A ) and loss in hardness vs. time ( FIG. 5B ) at 600° C. (referred to in the tempering resistance text).
  • FIG. 6 compares the results of impact toughness tests conducted for two types of transverse test specimens: unnotched (7 mm ⁇ 10 mm section, as per NADCA) or Charpy V, with 10 mm ⁇ 10 mm section and V notch. All materials treated to hardness 45 HRC according to the parameters of FIG. 5 a.
  • FIG. 7 shows the hardness profile of the nitrified layer of alloys PI 1, PI 2 and PI 3 vs. steel H13.
  • a plasma nitriding process was conducted for steel H13. Prior to nitriding, all sample alloys were quenched and tempered such to reach 45 HRC.
  • Hardness after tempering at 600° C. is shown in FIG. 1 , highlighting the effects of reduced Mo and Cr contents, and also the effect of higher C content.
  • Mo content a lower Mo concentration results in lower hardness after tempering.
  • Cr content drops, post-tempering hardness rises.
  • a possibility is that a lower Cr content reduces the amount of M 7 C 3 which, in turn, dissolves Mo.
  • a higher content of free Mo should be present in alloys of lower Cr content, which explains a more intense response to tempering.
  • the required hardness can be obtained by tempering at lower temperatures.
  • the ideal tempering temperature should be 50 to 80° C. above the working temperature to provide proper tempering resistance.
  • the typical tempering temperature should be 600° C.
  • Table 1 Chemical compositions adopted for samples from the same heat with variation of a single element.
  • the asterisks used in the Cr and Mo fields of the table below indicate that several compositions using this base were produced for the same heat, increasing the content of this element, but keeping the base composition of the heat.
  • Base 1 Base 2
  • Base 3 H13 Variation of . . . Mo Cr C — C 0.36 0.36 0.48 0.37 Si 0.32 0.32 0.32 0.92 Mn 0.26 0.28 0.27 0.31
  • P 0.007 0.006 0.006 0.022 S 0.001 0.002 0.001 0.001 Co 0.02 0.02 0.02 0.02 Cr 5.00 ** *** 4.82 Mo * 0.65 0.6 1.17 Ni 0.15 0.06 0.06 0.11 V 0.4 0.41 0.41 0.79 W 0.01 0.01 0.01 0.09 Cu 0.02 0.03 0.03 0.03 Al 0.013 ⁇ 0.005 ⁇ 0.005 0.02 * Mo variation: 0.05; 0.30; 0.60; 0.90; 1.22; 1.51 ** Cr variation, considering 0.36% C: 2.0; 3.0; 4.0; 5.1; 6.2; 7.1, *** Cr variation, considering 0.48% C: 2.0; 3.0; 4.0; 5.1; 6.1; 7.0;
  • the C effect is related to increased formation of secondary carbides and, when associated with a lower Cr content, it provides the hardness required to start the work, even in alloys of lower Mo content (half of steel H13). In alloys of higher C content, a similar Cr effect can be observed.
  • the new alloys can reach similar results in terms of hardness at 600° C. ( FIG. 5 a ), or even better, in terms of tempering resistance, if compared to steel H13 ( FIG. 5 b ).
  • FIG. 6 Another important point can be compared in FIG. 6 , in terms of toughness.
  • the toughness of the alloy of the present invention when bearing low Al contents, is equivalent to that of steel H13. This demonstrates that the low Si and P contents of alloy PI1 compensate for the loss of toughness likely to occur as the C content increases in relation to steel H13.
  • FIG. 6 also shows that toughness is inversely proportional to the Al content.
  • alloy PI2 becomes interesting for having toughness>200 J and extremely high hardness of the nitrified layer (almost 1400 HV). Alloy PI 3 does not show gains in terms of the nitrified layer, but toughness is far lower.
  • alloy PI1 seems more appropriate, also showing hardness after nitriding similar to that of steel H13, reaching more than 1000 HV on surface, which is the typical specification for extrusion tools. Furthermore, as previously shown in FIG. 5 , alloy PI 1 also presents improved hot strength properties. Therefore, considering the properties required for hot work applications, the alloys of the present invention show results equivalent to or better than those of steel H13. Such results are quite relevant for non-ferrous alloy extrusion dies, e.g., Al alloys, or hot forging dies.
  • Alloy PI 1 has improved tempering resistance, but hardness after nitriding and toughness equivalent to steel H13, while alloy PI 2 has lower toughness, but tempering resistance and hardness after nitriding significantly higher than steel H13.
  • the alloy should be selected on the basis of the most critical properties required for the application. However, in all cases, significant cost reductions can be obtained due to the low Mo and V content of the alloys of the present invention.

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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)
  • Heat Treatment Of Articles (AREA)
  • Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
  • Powder Metallurgy (AREA)
  • Manufacture Of Metal Powder And Suspensions Thereof (AREA)
US13/583,288 2010-03-08 2011-03-04 Tool steel for extrusion Abandoned US20130243639A1 (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
BRPI1003185-5A BRPI1003185A2 (pt) 2010-03-08 2010-03-08 aço para ferramentas de extrusão
BRPI1003185-5 2010-03-08
PCT/BR2011/000059 WO2011109881A1 (pt) 2010-03-08 2011-03-04 Aço para ferramentas de extrusão

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US (1) US20130243639A1 (ko)
EP (1) EP2546374A4 (ko)
JP (1) JP2013521411A (ko)
KR (1) KR20130004591A (ko)
CN (1) CN103097562A (ko)
BR (1) BRPI1003185A2 (ko)
CA (1) CA2792615A1 (ko)
MX (1) MX2012010394A (ko)
RU (1) RU2012142660A (ko)
WO (1) WO2011109881A1 (ko)
ZA (1) ZA201207378B (ko)

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CN115418467A (zh) * 2022-09-27 2022-12-02 江苏隆达超合金股份有限公司 一种铜镍合金管挤压用h13穿孔针热处理工艺

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CN103334054A (zh) * 2013-06-18 2013-10-02 上海大学 经济型含铝热挤压模具钢及其制备、热处理和表面处理方法
JP6410612B2 (ja) * 2015-01-08 2018-10-24 日産自動車株式会社 窒化部材及びそれを用いた摩擦伝動変速機
CN104805362A (zh) * 2015-03-31 2015-07-29 吉林大学 含铝中合金铸造冷作模具钢
KR101676244B1 (ko) 2015-04-14 2016-11-29 현대자동차주식회사 열변형 저감 스티어링 랙바용 탄소강 조성물 및 이의 제조방법
CN104805366B (zh) * 2015-05-20 2017-05-24 中南大学 一种粉末冶金低合金钢及其制备方法
JP2020132891A (ja) * 2019-02-12 2020-08-31 山陽特殊製鋼株式会社 熱伝導率に優れる金型用鋼
CN116810360A (zh) * 2023-06-30 2023-09-29 安徽铜都流体科技股份有限公司 一种可更换式刀箱制作方法

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WO2010044740A1 (en) * 2008-10-16 2010-04-22 Uddeholm Tooling Aktiebolag Steel material and a method for its manufacture

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US6478898B1 (en) * 1999-09-22 2002-11-12 Sumitomo Metal Industries, Ltd. Method of producing tool steels
JP3612459B2 (ja) * 1999-11-09 2005-01-19 山陽特殊製鋼株式会社 小ロット生産用金型鋼
CN1138017C (zh) * 2000-06-08 2004-02-11 顺德市世创金属科技有限公司 一种中合金铬系热作模具钢
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WO2010044740A1 (en) * 2008-10-16 2010-04-22 Uddeholm Tooling Aktiebolag Steel material and a method for its manufacture

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Publication number Priority date Publication date Assignee Title
CN115418467A (zh) * 2022-09-27 2022-12-02 江苏隆达超合金股份有限公司 一种铜镍合金管挤压用h13穿孔针热处理工艺

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MX2012010394A (es) 2012-10-05
EP2546374A4 (en) 2015-02-18
BRPI1003185A2 (pt) 2012-02-07
JP2013521411A (ja) 2013-06-10
EP2546374A1 (en) 2013-01-16
CA2792615A1 (en) 2011-09-15
ZA201207378B (en) 2013-06-26
CN103097562A (zh) 2013-05-08
RU2012142660A (ru) 2014-04-20
KR20130004591A (ko) 2013-01-11
WO2011109881A1 (pt) 2011-09-15

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